Multi-level graphene-protected battery cathode active material particles

ABSTRACT

Provided is graphene-embraced particulate for use as a lithium-ion battery anode active material, wherein the particulate comprises primary particle(s) of an anode active material and multiple sheets of a first graphene material overlapped together to embrace or encapsulate the primary particle(s) and wherein a single or a plurality of graphene-encapsulated primary particles, along with an optional conductive additive, are further embraced or encapsulated by multiple sheets of a second graphene material, wherein the first graphene and the second graphene material is each in an amount from 0.01% to 20% by weight and the optional conductive additive is in an amount from 0% to 50% by weight, all based on the total weight of the particulate. Also provided are an anode and a battery comprising multiple graphene-embraced particulates.

FIELD OF THE INVENTION

The present invention relates generally to the field of lithiumbatteries and, in particular, to graphene-protected electrode activematerials for lithium batteries.

BACKGROUND A Review on Anode Active Materials

The most commonly used anode materials for lithium-ion batteries arenatural graphite and synthetic graphite (or artificial graphite) thatcan be intercalated with lithium and the resulting graphiteintercalation compound (GIC) may be expressed as Li_(x)C₆, where x istypically less than 1. The maximum amount of lithium that can bereversibly intercalated into the interstices between graphene planes ofa perfect graphite crystal corresponds to x=1, defining a theoreticalspecific capacity of 372 mAh/g.

Graphite or carbon anodes can have a long cycle life due to the presenceof a protective surface-electrolyte interface layer (SEI), which resultsfrom the reaction between lithium and the electrolyte (or betweenlithium and the anode surface/edge atoms or functional groups) duringthe first several charge-discharge cycles. The lithium in this reactioncomes from some of the lithium ions originally intended for the chargetransfer purpose. As the SEI is formed, the lithium ions become part ofthe inert SEI layer and become irreversible, i.e. they can no longer bethe active element for charge transfer. Therefore, it is desirable touse a minimum amount of lithium for the formation of an effective SEIlayer. In addition to SEI formation, the irreversible capacity lossQ_(ir) can also be attributed to graphite exfoliation caused byelectrolyte/solvent co-intercalation and other side reactions.

In addition to carbon- or graphite-based anode materials, otherinorganic materials that have been evaluated for potential anodeapplications include metal oxides, metal nitrides, metal sulfides, andthe like, and a range of metals, metal alloys, and intermetalliccompounds that can accommodate lithium atoms/ions or react with lithium.Among these materials, lithium alloys having a composition formula ofLi_(a)A (A is a metal such as Al, and “a” satisfies 0<a #5) are of greatinterest due to their high theoretical capacity, e.g., Li₄Si (3,829mAh/g), Li_(4.4)Si (4,200 mAh/g), Li_(4.4)Ge (1,623 mAh/g), Li_(4.4)Sn(993 mAh/g), Li₃Cd (715 mAh/g), Li₃Sb (660 mAh/g), Li_(4.4)Pb (569mAh/g), LiZn (410 mAh/g), and Li₃Bi (385 mAh/g). However, in the anodescomposed of these materials, severe pulverization (fragmentation of thealloy particles) occurs during the charge and discharge cycles due toexpansion and contraction of the anode active material induced by theinsertion and extraction of the lithium ions in and out of the anodeactive material. The expansion and contraction, and the resultingpulverization of active material particles lead to loss of contactsbetween active particles and conductive additives and loss of contactsbetween the anode active material and its current collector. Thisdegradation phenomenon is illustrated in FIG. 1. These adverse effectsresult in a significantly shortened charge-discharge cycle life.

To overcome the problems associated with such mechanical degradation,three technical approaches have been proposed:

-   (1) reducing the size of the active material particle, presumably    for the purpose of reducing the strain energy that can be stored in    a particle, which is a driving force for crack formation in the    particle. However, a reduced particle size implies a higher surface    area available for potentially reacting with the liquid electrolyte.    Such a reaction is undesirable since it is a source of irreversible    capacity loss.-   (2) depositing the electrode active material in a thin film form    directly onto a current collector, such as a copper foil. However,    such a thin film structure with an extremely small    thickness-direction dimension (typically much smaller than 500 nm,    often necessarily thinner than 100 nm) implies that only a small    amount of active material can be incorporated in an electrode (given    the same electrode or current collector surface area), providing a    low total lithium storage capacity and low lithium storage capacity    per unit electrode surface area (even though the capacity per unit    mass can be large). Such a thin film must have a thickness less than    100 nm to be more resistant to cycling-induced cracking, further    diminishing the total lithium storage capacity and the lithium    storage capacity per unit electrode surface area. Such a thin-film    battery has very limited scope of application. A desirable and    typical electrode thickness is from 100 m to 200 μm. These thin-film    electrodes (with a thickness of <500 nm or even <100 nm) fall short    of the required thickness by three (3) orders of magnitude, not just    by a factor of 3.-   (3) using a composite composed of small electrode active particles    protected by (dispersed in or encapsulated by) a less active or    non-active matrix, e.g., carbon-coated Si particles, sol gel    graphite-protected Si, metal oxide-coated Si or Sn, and    monomer-coated Sn nanoparticles. Presumably, the protective matrix    provides a cushioning effect for particle expansion or shrinkage,    and prevents the electrolyte from contacting and reacting with the    electrode active material. Examples of anode active particles are    Si, Sn, and SnO₂. Unfortunately, when an active material particle,    such as Si particle, expands during the battery charge step, the    protective coating is easily broken due to the mechanical weakness    and/or brittleness of the protective coating materials. There has    been no high-strength and high-toughness material available that is    itself also lithium ion conductive.

It may be further noted that the coating or matrix materials used toprotect active particles (such as Si and Sn) are carbon, sol gelgraphite, metal oxide, monomer, ceramic, and lithium oxide. Theseprotective materials alone are all very brittle, weak (of low strength),and/or non-conducting (e.g., ceramic or oxide coating). Ideally, theprotective material should meet the following requirements: (a) Thecoating or matrix material should be of high strength and stiffness sothat it can help to refrain the electrode active material particles,when lithiated, from expanding to an excessive extent. (b) Theprotective material should also have high fracture toughness or highresistance to crack formation to avoid disintegration during repeatedcycling. (c) The protective material must be inert (inactive) withrespect to the electrolyte, but be a good lithium ion conductor. (d) Theprotective material must not provide any significant amount of defectsites that irreversibly trap lithium ions. (e) The protective materialmust be lithium ion conductive. The prior art protective materials allfall short of these requirements. Hence, it was not surprising toobserve that the resulting anode typically shows a reversible specificcapacity much lower than expected. In many cases, the first-cycleefficiency is extremely low (mostly lower than 80% and some even lowerthan 60%). Furthermore, in most cases, the electrode was not capable ofoperating for a large number of cycles. Additionally, most of theseelectrodes are not high-rate capable, exhibiting unacceptably lowcapacity at a high discharge rate.

Due to these and other reasons, most of prior art composite electrodeshave deficiencies in some ways, e.g., in most cases, less thansatisfactory reversible capacity, poor cycling stability, highirreversible capacity, ineffectiveness in reducing the internal stressor strain during the lithium ion insertion and extraction steps, andother undesirable side effects.

Complex composite particles of particular interest are a mixture ofseparate Si and graphite particles dispersed in a carbon matrix; e.g.those prepared by Mao, et al. [“Carbon-coated Silicon Particle Powder asthe Anode Material for Lithium Batteries and the Method of Making theSame,” US 2005/0136330 (Jun. 23, 2005)]. Also of interest are carbonmatrix-containing complex nano Si (protected by oxide) and graphiteparticles dispersed therein, and carbon-coated Si particles distributedon a surface of graphite particles Again, these complex compositeparticles led to a low specific capacity or can be charged-dischargedfor up to a small number of cycles only. It appears that carbon byitself is relatively weak and brittle and the presence of micron-sizedgraphite particles does not improve the mechanical integrity of carbonsince graphite particles are themselves relatively weak. Graphite wasused in these cases presumably for the purpose of improving theelectrical conductivity of the anode material. Furthermore, polymericcarbon, amorphous carbon, or pre-graphitic carbon may have too manylithium-trapping sites that irreversibly capture lithium during thefirst few cycles, resulting in excessive irreversibility.

In summary, the prior art has not demonstrated a composite material thathas all or most of the properties desired for use as an anode materialin a lithium-ion battery. Thus, there is an urgent and continuing needfor a new anode for the lithium-ion battery that has a high cycle life,high reversible capacity, low irreversible capacity, small particlesizes (for high-rate capacity), and compatibility with commonly usedelectrolytes. There is also a need for a method of readily or easilyproducing such a material in large quantities.

In response to these needs, one of our earlier applications discloses ananoscaled graphene platelet-based composite composition for use as alithium ion battery anode [A. Zhamu and B. Z. Jang, “NanographenePlatelet-Based Composite Anode Compositions for Lithium Ion Batteries,”U.S. patent application Ser. No. 11/982,672 (Nov. 5, 2007); Now U.S.Pat. No. 7,745,047 (Jun. 29, 2010)]. This composition comprises: (a)micron- or nanometer-scaled particles or coating of an anode activematerial; and (b) a plurality of nanoscaled graphene platelets (NGPs),wherein a platelet comprises a graphene sheet or a stack of graphenesheets having a platelet thickness less than 100 nm and wherein theparticles or coating are physically attached or chemically bonded toNGPs. Nanographene platelets (NGPs) are individual graphene sheets(individual basal planes of carbon atoms isolated from a graphitecrystal) or stacks of multiple graphene planes bonded together in thethickness direction. The NGPs have a thickness less than 100 nm and alength, width, or diameter that can be greater or less than 10 μm. Thethickness is more preferably less than 10 nm and most preferably lessthan 1 nm.

Disclosed in another patent application of ours is a more specificcomposition, which is composed of a 3-D network of NGPs and/or otherconductive filaments and select anode active material particles that arebonded to these NGPs or filaments through a conductive binder [JinjunShi, Aruna Zhamu and Bor Z. Jang, “Conductive Nanocomposite-basedElectrodes for Lithium Batteries,” U.S. patent application Ser. No.12/156,644 (Jun. 4, 2008) (U.S. Pat. Pub. No. 2009-0305135)]. Yetanother application, as schematically shown in FIG. 2(A) and FIG. 2(B),provides a nanographene-reinforced nanocomposite solid particlecomposition containing NGPs and electrode active material particles,which are both dispersed in a protective matrix (e.g. a carbon matrix)[Aruna Zhamu, Bor Z. Jang, and Jinjun Shi, “Nanographene ReinforcedNanocomposite for Lithium Battery Electrodes,” U.S. patent applicationSer. No. 12/315,555 (Dec. 4, 2008) (U.S. Pat. Pub. No. 2010-0143798)].

After our discovery of graphene providing an outstanding support foranode active materials, many subsequent studies by others have confirmedthe effectiveness of this approach. For instance, Wang, et al.investigated self-assembled TiO₂-graphene hybrid nanostructures forenhanced Li-ion insertion [D. Wang, et al. “Self-Assembled TiO₂-GrapheneHybrid Nanostructures for Enhanced Li-Ion Insertion.” ACS Nano, 3 (2009)907-914]. The results indicate that, as compared with the pure TiO₂phase, the specific capacity of the hybrid was more than doubled at highcharge rates. The improved capacity at a high charge-discharge rate wasattributed to increased electrode conductivity afforded by a percolatedgraphene network embedded into the metal oxide electrodes. However, allthese earlier studies were focused solely on providing a network ofelectron-conducting paths for the anode active material particles andfailed to address other critical issues, such as ease of anode materialprocessing, electrode processability, electrode tap density (the abilityto pack a dense mass into a given volume), and long-term cyclingstability. For instance, the method of preparing self-assembled hybridnanostructures is not amenable to mass production. The graphene oxidesheets used were made using an environmentally undesirable process priorto the assembling procedure. The anode material particle-coated graphenesheets alone are not suitable for electrode fabrication (due to thedifficulty in coating the materials onto a current collector), and theresulting electrodes are typically too low in the tap density.Additionally, paper-based composite structures are not compatible withcurrent lithium-ion battery production equipment. These are allcritically important issues that must be addressed in a real batterymanufacturing environment.

A Review on Cathode Active Materials

Due to extremely poor electrical conductivity of all cathode (positiveelectrode) active materials in a lithium-ion, lithium metal, orlithium-sulfur cell, a conductive additive (e.g. carbon black, finegraphite particles, expanded graphite particles, or their combinations),typically in the amount of 5%-20%, must be added into the electrode. Inthe case of a lithium-sulfur cell, a carbon amount as high as 50% byweight is used as a conductive support for sulfur in the cathode.However, the conductive additive is not an electrode active material(i.e. it is not capable of reversibly storing lithium ions). The use ofa non-active material means that the relative proportion of an electrodeactive material, such as LiFePO₄, is reduced or diluted. For instance,the incorporation of 5% by weight of PVDF as a binder and 5% of carbonblack as a conductive additive in a cathode would mean that the maximumamount of the cathode active material (e.g., lithium cobalt oxide) isonly 90%, effectively reducing the total lithium ion storage capacity.Since the specific capacities of the more commonly used cathode activematerials are already very low (140-170 mAh/g), this problem is furtheraggravated if a significant amount of non-active materials is used todilute the concentration of the active material.

State-of-the-art carbon black (CB) materials, as a conductive additive,have several drawbacks:

-   -   (1) CBs are typically available in the form of aggregates of        multiple primary particles that are typically spherical in        shape. Due to this geometric feature (largest        dimension-to-smallest dimension ratio or aspect ratio˜1) and the        notion that CBs are a minority phase dispersed as discrete        particles in an electrically insulating matrix (e.g. lithium        cobalt oxide and lithium iron phosphate), a large amount of CBs        is required to reach a percolation threshold where the CB        particles are combined to form a 3-D network of        electron-conducting paths.    -   (2) CBs themselves have a relatively low electrical conductivity        and, hence, the resulting electrode remains to be of relatively        low conductivity even when the percolation threshold is reached.        A relatively high proportion of CBs (far beyond the percolation        threshold) must be incorporated in the cathode to make the        resulting composite electrode reasonably conducting.

Clearly, an urgent need exists for a more effective electricallyconductive additive material. Preferably, this electrically conductiveadditive is also of high thermal conductivity. Such a thermallyconductive additive would be capable of dissipating the heat generatedfrom the electrochemical operation of the Li-ion battery, therebyincreasing the reliability of the battery and decreasing the likelihoodthat the battery will suffer from thermal runaway and rupture. With ahigh electrical conductivity, there would be no need to add a highproportion of conductive additives.

There have been several attempts to use other carbon nanomaterials thancarbon black (CB) or acetylene black (AB) as a conductive additive forthe cathode of a lithium battery. These include carbon nanotubes (CNTs),vapor-grown carbon nanofibers (VG-CNFs), and simple carbon coating onthe surface of cathode active material particles. The result has notbeen satisfactory and hence, as of today, carbon black and artificialgraphite particles are practically the only two types of cathodeconductive additives widely used in lithium ion battery industry. Thereasons are beyond just the obvious high costs of both CNTs and VG-CNFs.The difficulty in disentangling CNTs and VG-CNFs and uniformlydispersing them in a liquid or solid medium has been an impediment tothe more widespread utilization of these expensive materials as aconductive additive. Additionally, the production of both CNTs andVG-CNFs normally require the use of a significant amount of transitionmetal nanoparticles as a catalyst. It is difficult to remove andimpossible to totally remove these transition metal particles, which canhave adverse effect on the cycling stability of a lithium metal.

As for the less expensive carbon coating, being considered for use inlithium iron phosphate, the conductivity of the carbon coating(typically obtained by converting a precursor such as sugar or resin viapyrolyzation) is relatively low. It would take a graphitizationtreatment to render the carbon coating more conductive, but thistreatment requires a temperature higher than 2,000° C., which woulddegrade the underlying cathode active material (e.g., LiFePO₄).

As an alternative approach, Ding, et al investigated the electrochemicalbehavior of LiFePO₄/graphene composites [Y. Ding, et al. “Preparation ofnanostructured LiFePO₄/graphene composites by co-precipitation method,”Electrochemistry Communications 12 (2010) 10-13]. The co-precipitationmethod leads to the formation of LiFePO₄ nanoparticles coated on bothprimary surfaces of graphene nanosheets. The cathode is then prepared bystacking these LiFePO₄-coated graphene sheets together. This approachhas several major drawbacks:

-   -   (1) With the two primary surfaces of a graphene sheet attached        with LiFePO₄ nanoparticles, the resulting electrode entails many        insulator-to-insulator contacts between two adjoining coated        sheets in a stack.    -   (2) Only less than 30% of the graphene surface area is covered        by LiFePO₄ particles on either side. This is a relatively low        proportion of the cathode active material.    -   (3) The LiFePO₄ particles are easily detached from graphene        sheets during handling and electrode production.    -   (4) We have found that the nanoparticle-attached graphene sheets        as prepared by the co-precipitation method are not amenable to        fabrication of cathodes with current electrode coating        equipment. In particular, these particle-attached graphene        sheets could not be compacted into a dense state with a high        mass per unit electrode volume. In other words, the cathode tap        density is relatively low. This is a very serious issue since        all of the commonly used cathode active materials, including        LiFePO₄, already have a very low specific capacity (mAh/g), and        not being able to pack a large mass of a cathode active material        into a given electrode volume would mean an excessively low        overall capacity at the cathode side. (It may be noted that the        typical specific capacity (140-170 mAh/g) of a cathode active        material is already much lower than that (330-360 mAh/g) of an        anode active material. Such an imbalance has been a major issue        in the design and fabrication of lithium ion batteries.)

A Review on Graphene (Isolated Graphene Sheets or NanographenePlatelets)

A single-layer graphene sheet is composed of carbon atoms occupying atwo-dimensional hexagonal lattice. Multi-layer graphene is a plateletcomposed of more than one graphene plane. Individual single-layergraphene sheets and multi-layer graphene platelets are hereincollectively called nanographene platelets (NGPs) or graphene materials.NGPs include pristine graphene (essentially 99% of carbon atoms),slightly oxidized graphene (<5% by weight of oxygen), graphene oxide(≥5% by weight of oxygen), slightly fluorinated graphene (<5% by weightof fluorine), graphene fluoride ((≥5% by weight of fluorine), otherhalogenated graphene, and chemically functionalized graphene.

NGPs have been found to have a range of unusual physical, chemical, andmechanical properties. For instance, graphene was found to exhibit thehighest intrinsic strength and highest thermal conductivity of allexisting materials. Although practical electronic device applicationsfor graphene (e.g., replacing Si as a backbone in a transistor) are notenvisioned to occur within the next 5-10 years, its application as ananofiller in a composite material and an electrode material in energystorage devices is imminent. The availability of processable graphenesheets in large quantities is essential to the success in exploitingcomposite, energy, and other applications for graphene.

Our research group was among the first to discover graphene [B. Z. Jangand W. C. Huang, “Nanoscaled Graphene Plates,” U.S. patent applicationSer. No. 10/274,473, submitted on Oct. 21, 2002; now U.S. Pat. No.7,071,258 (Jul. 4, 2006)]. The processes for producing NGPs and NGPnanocomposites were recently reviewed by us [Bor Z. Jang and A Zhamu,“Processing of Nanographene Platelets (NGPs) and NGP Nanocomposites: AReview,” J. Materials Sci. 43 (2008) 5092-5101]. Our research hasyielded a process for chemical-free production of isolated nanographeneplatelets that is novel in that is does not follow the establishedmethods for production of nanographene platelets outlined below. Inaddition, the process is of enhanced utility in that it is costeffective, and provided novel graphene materials with significantlyreduced environmental impact. Four main prior-art approaches have beenfollowed to produce NGPs. Their advantages and shortcomings are brieflysummarized as follows:

Prior Art Method for Production of Isolated Graphene Sheets (NGPs)

Approach 1: Chemical Formation and Reduction of Graphite Oxide (GO)Platelets

The first approach (FIG. 1) entails treating natural graphite powderwith an intercalant and an oxidant (e.g., concentrated sulfuric acid andnitric acid, respectively) to obtain a graphite intercalation compound(GIC) or, actually, graphite oxide (GO). [William S. Hummers, Jr., etal., Preparation of Graphitic Oxide, Journal of the American ChemicalSociety, 1958, p. 1339.] Prior to intercalation or oxidation, graphitehas an inter-graphene plane spacing of approximately 0.335 nm (L_(d)=½d₀₀₂=0.335 nm). With an intercalation and oxidation treatment, theinter-graphene spacing is increased to a value typically greater than0.6 nm. This is the first expansion stage experienced by the graphitematerial during this chemical route. The obtained GIC or GO is thensubjected to further expansion (often referred to as exfoliation) usingeither a thermal shock exposure or a solution-based,ultrasonication-assisted graphene layer exfoliation approach.

In the thermal shock exposure approach, the GIC or GO is exposed to ahigh temperature (typically 800-1,050° C.) for a short period of time(typically 15 to 60 seconds) to exfoliate or expand the GIC or GO forthe formation of exfoliated or further expanded graphite, which istypically in the form of a “graphite worm” composed of graphite flakesthat are still interconnected with one another. This thermal shockprocedure can produce some separated graphite flakes or graphene sheets,but normally the majority of graphite flakes remain interconnected.Typically, the exfoliated graphite or graphite worm is then subjected toa flake separation treatment using air milling, mechanical shearing, orultrasonication in water. Hence, approach 1 basically entails threedistinct procedures: first expansion (oxidation or intercalation),further expansion (or “exfoliation”), and separation.

In the solution-based separation approach, the expanded or exfoliated GOpowder is dispersed in water or aqueous alcohol solution, which issubjected to ultrasonication. It is important to note that in theseprocesses, ultrasonification is used after intercalation and oxidationof graphite (i.e., after first expansion) and typically after thermalshock exposure of the resulting GIC or GO (after second expansion).Alternatively, the GO powder dispersed in water is subjected to an ionexchange or lengthy purification procedure in such a manner that therepulsive forces between ions residing in the inter-planar spacesovercome the inter-graphene van der Waals forces, resulting in graphenelayer separations.

There are several major problems associated with this conventionalchemical production process:

-   -   (1) The process requires the use of large quantities of several        undesirable chemicals, such as sulfuric acid, nitric acid, and        potassium permanganate or sodium chlorate.    -   (2) The chemical treatment process requires a long intercalation        and oxidation time, typically 5 hours to five days.    -   (3) Strong acids consume a significant amount of graphite during        this long intercalation or oxidation process by “eating their        way into the graphite” (converting graphite into carbon dioxide,        which is lost in the process). It is not unusual to lose 20-50%        by weight of the graphite material immersed in strong acids and        oxidizers.    -   (4) The thermal exfoliation requires a high temperature        (typically 800-1,200° C.) and, hence, is a highly        energy-intensive process.    -   (5) Both heat- and solution-induced exfoliation approaches        require a very tedious washing and purification step. For        instance, typically 2.5 kg of water is used to wash and recover        1 gram of GIC, producing huge quantities of waste water that        need to be properly treated.    -   (6) In both the heat- and solution-induced exfoliation        approaches, the resulting products are GO platelets that must        undergo a further chemical reduction treatment to reduce the        oxygen content. Typically even after reduction, the electrical        conductivity of GO platelets remains much lower than that of        pristine graphene. Furthermore, the reduction procedure often        involves the utilization of toxic chemicals, such as hydrazine.    -   (7) Furthermore, the quantity of intercalation solution retained        on the flakes after draining may range from 20 to 150 parts of        solution by weight per 100 parts by weight of graphite flakes        (pph) and more typically about 50 to 120 pph. During the        high-temperature exfoliation, the residual intercalate species        retained by the flakes decompose to produce various species of        sulfuric and nitrous compounds (e.g., NO_(x) and SO_(N)), which        are undesirable. The effluents require expensive remediation        procedures in order not to have an adverse environmental impact.        Approach 2: Direct Formation of Pristine Nanographene Platelets

In 2002, our research team succeeded in isolating single-layer andmulti-layer graphene sheets from partially carbonized or graphitizedpolymeric carbons, which were obtained from a polymer or pitch precursor[B. Z. Jang and W. C. Huang, “Nanoscaled Graphene Plates,” U.S. patentapplication Ser. No. 10/274,473, submitted on Oct. 21, 2002; now U.S.Pat. No. 7,071,258 (Jul. 4, 2006)]. Mack, et al [“Chemical manufactureof nanostructured materials” U.S. Pat. No. 6,872,330 (Mar. 29, 2005)]developed a process that involved intercalating graphite with potassiummelt and contacting the resulting K-intercalated graphite with alcohol,producing violently exfoliated graphite containing NGPs. The processmust be carefully conducted in a vacuum or an extremely dry glove boxenvironment since pure alkali metals, such as potassium and sodium, areextremely sensitive to moisture and pose an explosion danger. Thisprocess is not amenable to the mass production of NGPs.

Approach 3: Epitaxial Growth and Chemical Vapor Deposition of GrapheneSheets on Inorganic Crystal Surfaces

Small-scale production of ultra-thin graphene sheets on a substrate canbe obtained by thermal decomposition-based epitaxial growth and a laserdesorption-ionization technique. [Walt A. DeHeer, Claire Berger, PhillipN. First, “Patterned thin film graphite devices and method for makingsame” U.S. Pat. No. 7,327,000 B2 (Jun. 12, 2003)] Epitaxial films ofgraphite with only one or a few atomic layers are of technological andscientific significance due to their peculiar characteristics and greatpotential as a device substrate. However, these processes are notsuitable for mass production of isolated graphene sheets for compositematerials and energy storage applications.

Approach 4: The Bottom-Up Approach (Synthesis of Graphene from SmallMolecules)

Yang, et al. [“Two-dimensional Graphene Nano-ribbons,” J. Am. Chem. Soc.130 (2008) 4216-17] synthesized nanographene sheets with lengths of upto 12 nm using a method that began with Suzuki-Miyaura coupling of1,4-diiodo-2,3,5,6-tetraphenyl-benzene with 4-bromophenylboronic acid.The resulting hexaphenylbenzene derivative was further derivatized andring-fused into small graphene sheets. This is a slow process that thusfar has produced very small graphene sheets.

Thus, an urgent need exists to have a graphene production process thatrequires a reduced amount of undesirable chemical (or elimination ofthese chemicals all together), shortened process time, less energyconsumption, lower degree of graphene oxidation, reduced or eliminatedeffluents of undesirable chemical species into the drainage (e.g.,sulfuric acid) or into the air (e.g., SO₂ and NO₂). The process shouldbe able to produce more pristine (less oxidized and damaged), moreelectrically conductive, and larger/wider graphene sheets.

Using the lithium-ion battery and lithium metal battery as examples,these graphene sheets must be effective in (a) protecting anode activematerials or cathode active materials (e.g. against volumeexpansion/shrinkage-induced pulverization and repeated SEI formation)and the electrodes (against excessive volume changes of both anode andcathode) during repeated battery charges/discharges for improved cyclestability and (b) providing a 3D network of electron-conducting pathwayswithout the use of an excessive amount of conductive additives that arenon-active materials (that adds weight and volume to the battery withoutproviding additional capacity of storing lithium ions).

Most desirably, a need exists for a process that is capable of producingisolated graphene sheets directly from a graphitic material and,concurrently, transferring the graphene sheets to wrap around, embraceor encapsulate the primary particles of an anode active material orcathode active material. These graphene sheets must be arranged in astructure capable of preventing rapid capacity decay.

In short, the present invention was made to overcome the aforementionedlimitations of current lithium batteries and the graphene materials usedto protect these batteries.

SUMMARY OF THE INVENTION

It may be noted that the word “electrode” herein refers to either ananode (negative electrode) or a cathode (positive electrode) of abattery. These definitions are also commonly accepted in the art ofbatteries or electrochemistry.

The present invention provides a graphene-embraced particulate(secondary particle) for use as a lithium-ion battery electrode activematerial (anode or cathode active material), wherein the particulatecomprises a single or a plurality of graphene-encapsulated primaryparticles of an anode active material or a cathode active material,having a size from 5 nm to 20 μm, wherein the graphene-encapsulatedprimary particle is composed of a primary particle of the electrodeactive material and multiple sheets of a first graphene materialoverlapped together to embrace or encapsulate the primary particle andwherein the single or a plurality of graphene-encapsulated primaryparticles, along with an optional conductive additive, are furtherembraced or encapsulated by multiple sheets of a second graphenematerial, wherein the first graphene material is the same as ordifferent from the second graphene material, and wherein the firstgraphene material and the second graphene material is each in an amountfrom 0.01% to 20% by weight and the optional conductive additive is inan amount from 0% to 50% by weight, all based on the total weight of theparticulate. In some embodiments, the particulate is spherical orellipsoidal in shape.

The first graphene material or the second graphene material preferablycomprises single-layer graphene or few-layer graphene, wherein thefew-layer graphene is defined as a graphene sheet or platelet formed of2-10 graphene planes. There are multiple single-layer or few-layergraphene sheets/platelets wrapping around one primary particle or a fewprimary particles clustered together.

In some embodiments, the first graphene material or the second graphenematerial is selected from pristine graphene, graphene oxide, reducedgraphene oxide, graphene fluoride, graphene chloride, graphene bromide,graphene iodide, hydrogenated graphene, nitrogenated graphene,chemically functionalized graphene, or a combination thereof.

In certain preferred embodiments, the first graphene material isdifferent than the second graphene material. In some embodiments, thefirst graphene material contains pristine graphene and the secondgraphene material is selected from graphene oxide, reduced grapheneoxide, graphene fluoride, graphene chloride, graphene bromide, grapheneiodide, hydrogenated graphene, nitrogenated graphene, chemicallyfunctionalized graphene, or a combination thereof.

In some embodiments, the first graphene material contains pristinegraphene or a first chemically functionalized graphene and the secondgraphene material is selected from graphene oxide, reduced grapheneoxide, graphene fluoride, graphene chloride, graphene bromide, grapheneiodide, hydrogenated graphene, nitrogenated graphene, a secondchemically functionalized graphene, or a combination thereof, whereinthe first chemically functionalized graphene is different than thesecond chemically functionalized graphene.

In certain embodiments, the anode active material comprises an elementselected from Si, Ge, Sn, Cd, Sb, Pb, Bi, Zn, Al, Co, Ni, or Ti.

In some embodiments, the anode active material is selected from thegroup consisting of: (a) lithiated and un-lithiated silicon (Si),germanium (Ge), tin (Sn), lead (Pb), antimony (Sb), bismuth (Bi), zinc(Zn), aluminum (Al), titanium (Ti), nickel (Ni), cobalt (Co), andcadmium (Cd); (b) lithiated and un-lithiated alloys or intermetalliccompounds of Si, Ge, Sn, Pb, Sb, Bi, Zn, Al, Ti, Ni, Co, or Cd withother elements; (c) lithiated and un-lithiated oxides, carbides,nitrides, sulfides, phosphides, selenides, and tellurides of Si, Ge, Sn,Pb, Sb, Bi, Zn, Al, Ti, Fe, Ni, Co, Mn, V, or Cd, and their mixtures,composites, or lithium-containing composites; (d) lithiated andun-lithiated salts and hydroxides of Sn; (e) lithium titanate, lithiummanganate, lithium aluminate, lithium-containing titanium oxide, lithiumtransition metal oxide; and combinations thereof.

In certain embodiments, the primary particles of anode active materialare selected from lithiated titanium dioxide, lithiated titanium oxide,lithium titanate, or Li₄Ti₅O₁₂.

In some embodiments, the primary particles of anode active material areselected from natural graphite, artificial graphite, mesocarbonmicrobead (MCMB), graphitic coke, mesophase carbon, hard carbon, softcarbon, polymeric carbon, carbon or graphite fiber segments, carbonnanofiber or graphitic nanofiber, carbon nanotube, or a combinationthereof.

The electrode active material may be a cathode active material selectedfrom an inorganic material, an organic or polymeric material, a metaloxide/phosphate/sulfide, or a combination thereof. The metaloxide/phosphate/sulfide may be selected from a lithium cobalt oxide,lithium nickel oxide, lithium manganese oxide, lithium vanadium oxide,lithium-mixed metal oxide, lithium iron phosphate, lithium manganesephosphate, lithium vanadium phosphate, lithium mixed metal phosphate,sodium cobalt oxide sodium nickel oxide, sodium manganese oxide, sodiumvanadium oxide, sodium-mixed metal oxide, sodium iron phosphate, sodiummanganese phosphate, sodium vanadium phosphate, sodium mixed metalphosphate, transition metal sulfide, lithium polysulfide, sodiumpolysulfide, magnesium polysulfide, or a combination thereof.

In some embodiments, the electrode active material may be a cathodeactive material selected from sulfur, sulfur compound, sulfur-carboncomposite, sulfur-polymer composite, lithium polysulfide, transitionmetal dichalcogenide, a transition metal trichalcogenide, or acombination thereof. The inorganic material may be selected from TiS₂,TaS₂, MoS₂, NbSe₃, MnO₂, COO₂, an iron oxide, a vanadium oxide, or acombination thereof.

The metal oxide/phosphate/sulfide contains a vanadium oxide selectedfrom the group consisting of VO₂, Li_(x)VO₂, V₂O₅, Li_(x)V₂O₅, V₃O₈,Li_(x)V₃O₈, Li_(x)V₃O₇, V₄O₉, Li_(x)V₄O₉, V₆O₁₃, Li_(x)V₆O₁₃, theirdoped versions, their derivatives, and combinations thereof, wherein0.1<x<5.

In some embodiments, the metal oxide/phosphate/sulfide is selected froma layered compound LiMO₂, spinel compound LiM₂O₄, olivine compoundLiMPO₄, silicate compound Li₂MSiO₄, Tavorite compound LiMPO₄F, boratecompound LiMBO₃, or a combination thereof, wherein M is a transitionmetal or a mixture of multiple transition metals.

The inorganic material may be selected from: (a) bismuth selenide orbismuth telluride, (b) transition metal dichalcogenide ortrichalcogenide, (c) sulfide, selenide, or telluride of niobium,zirconium, molybdenum, hafnium, tantalum, tungsten, titanium, cobalt,manganese, iron, nickel, or a transition metal; (d) boron nitride, or(e) a combination thereof.

The organic material or polymeric material is selected frompoly(anthraquinonyl sulfide) (PAQS), a lithium oxocarbon,3,4,9,10-perylenetetracarboxylic dianhydride (PTCDA),poly(anthraquinonyl sulfide), pyrene-4,5,9,10-tetraone (PYT),polymer-bound PYT, quino(triazene), redox-active organic material,tetracyanoquinodimethane (TCNQ), tetracyanoethylene (TCNE),2,3,6,7,10,11-hexamethoxytriphenylene (HMTP), poly(5-amino-1,4-dyhydroxyanthraquinone) (PADAQ), phosphazene disulfide polymer ([(NPS₂)₃]n),lithiated 1,4,5,8-naphthalenetetraol formaldehyde polymer,hexaazatrinaphtylene (HATN), hexaazatriphenylene hexacarbonitrile(HAT(CN)₆), 5-benzylidene hydantoin, isatine lithium salt, pyromelliticdiimide lithium salt, tetrahydroxy-p-benzoquinone derivatives (THQLi₄),N,N′-diphenyl-2,3,5,6-tetraketopiperazine (PHP),N,N′-diallyl-2,3,5,6-tetraketopiperazine (AP),N,N′-dipropyl-2,3,5,6-tetraketopiperazine (PRP), a thioether polymer, aquinone compound, 1,4-benzoquinone, 5,7,12,14-pentacenetetrone (PT),5-amino-2,3-dihydro-1,4-dyhydroxy anthraquinone (ADDAQ),5-amino-1,4-dyhydroxy anthraquinone (ADAQ), calixquinone, Li₄C₆O₆,Li₂C₆O₆, Li₆C₆O₆, or a combination thereof. These compounds arepreferably mixed with a conducting material to improve their electricalconductivity and rigidity so as to enable the peeling-off of graphenesheets from the graphitic material particles.

The thioether polymer in the above list may be selected frompoly[methanetetryl-tetra(thiomethylene)] (PMTTM),poly(2,4-dithiopentanylene) (PDTP), a polymer containingpoly(ethene-1,1,2,2-tetrathiol) (PETT) as a main-chain thioetherpolymers, a side-chain thioether polymer having a main-chain consistingof conjugating aromatic moieties, and having a thioether side chain as apendant, poly(2-phenyl-1,3-dithiolane) (PPDT),poly(1,4-di(1,3-dithiolan-2-yl)benzene) (PDDTB),poly(tetrahydrobenzodithiophene) (PTHBDT),poly[1,2,4,5-tetrakis(propylthio)benzene] (PTKPTB, orpoly[3,4(ethylenedithio)thiophene] (PEDTT).

In some embodiments, the organic material contains a phthalocyaninecompound selected from copper phthalocyanine, zinc phthalocyanine, tinphthalocyanine, iron phthalocyanine, lead phthalocyanine, nickelphthalocyanine, vanadyl phthalocyanine, fluorochromium phthalocyanine,magnesium phthalocyanine, manganous phthalocyanine, dilithiumphthalocyanine, aluminum phthalocyanine chloride, cadmiumphthalocyanine, chlorogallium phthalocyanine, cobalt phthalocyanine,silver phthalocyanine, a metal-free phthalocyanine, a chemicalderivative thereof, or a combination thereof. These compounds arepreferably mixed with a conducting material to improve their electricalconductivity and rigidity so as to enable the peeling-off of graphenesheets from the graphitic material particles.

Preferably, in the particulate, the primary particles of an electrodeactive material have a size from 10 nm to 1 μm, further preferably from10 nm to 100 nm.

The conductive additive may be selected from amorphous carbon, CVDcarbon, carbonized resin, expanded graphite platelet, carbon nanotube,carbon nanofiber, carbon fiber, graphite fiber, pitch, coke, carbonblack, acetylene black, activated carbon, pitch-derived soft carbon (asoft carbon is a carbon that can be graphitized at a temperature higherthan 2,500° C.), pitch-derived hard carbon (a carbon that cannot begraphitized at a temperature higher than 2,500° C.), natural graphiteparticle, artificial graphite particle, electron-conducting polymer,lithium ion-conducting polymer, or a combination thereof, wherein theconductive additive is in electronic contact with thegraphene-encapsulated primary particle.

The carbonized resin or polymeric carbon is obtained from pyrolyzationof a polymer selected from the group consisting of phenol-formaldehyde,polyacrylonitrile, styrene-based polymers, cellulosic polymers, epoxyresins, and combinations thereof.

The invention also provides a powder mass of multiple particulates asdefined above. Also provided is a lithium battery anode electrodecontaining a mass of multiple particulates of this type and optionalconductive filler (typically 0-15% by weight) and optional binder(typically 0-15% by weight). In some embodiments, the invention providesa lithium battery containing such an anode electrode.

The invention also provides a battery electrode containing the abovedefined graphene-embraced particulates as an anode active material,wherein the battery is a lithium-ion battery, lithium metal secondarybattery, lithium-sulfur battery, lithium-air battery, lithium-seleniumbattery, sodium-ion battery, sodium metal secondary battery,sodium-sulfur battery, sodium-air battery, magnesium-ion battery,magnesium metal battery, aluminum-ion battery, aluminum metal secondarybattery, zinc-ion battery, zinc metal battery, or zinc-air battery.

The present invention also provides a strikingly simple, fast, scalable,environmentally benign, and cost-effective method of producinggraphene-embraced (graphene-encapsulated) particulates or secondaryparticles containing graphene-encapsulated primary particles of anodeactive material for a wide variety of batteries.

This method entails producing single-layer or few layer graphene sheetsdirectly from a graphitic or carbonaceous material (a graphene sourcematerial) and immediately transferring these isolated (peeled-off)graphene sheets onto surfaces of electrode active material particles toform graphene-embraced or graphene-encapsulated primary particles ofanode active material. In an embodiment, the graphitic material orcarbonaceous material has never been intercalated, oxidized, orexfoliated and does not include previously produced isolated graphenesheets. These graphene-encapsulated primary particles are then combinedwith graphene sheets of the same or different type to make secondaryparticles, each typically containing a cluster of 1-1000graphene-encapsulated primary particles further embraced by graphenesheets.

Thus, the invention also provides a method of producing a mass ofgraphene-embraced particulates or secondary particles directly from agraphitic material for use as a lithium-ion battery anode activematerial. In some embodiments, the method comprises:

-   -   a) mixing multiple particles of a graphitic material and        multiple primary particles of a solid anode active material and        optional ball-milling media to form a mixture in an impacting        chamber of an energy impacting apparatus, wherein preferably the        graphitic material has never been previously intercalated,        oxidized, or exfoliated and the impacting chamber contains        therein no previously produced isolated graphene sheets;    -   b) operating the energy impacting apparatus with a frequency and        an intensity for a length of time sufficient for peeling off        graphene sheets from the particles of graphitic material and        transferring the peeled-off graphene sheets to surfaces of the        primary particles of the solid anode active material and fully        embrace or encapsulate the primary particles to produce        graphene-embraced or graphene-encapsulated primary particles of        the anode active material inside the impacting chamber;    -   c) recovering the graphene-embraced or graphene-encapsulated        primary particles from the impacting chamber, wherein at least        one of the embraced or encapsulated primary particles contains        multiple graphene sheets of a first graphene material fully        embracing or encapsulating at least one of the primary        particles; and    -   d) combining a mass of the recovered graphene-embraced or        graphene-encapsulated primary particles, an optional conductive        additive, and graphene sheets of a second graphene material into        a mass of graphene-embraced particulates (e.g. via spray-drying,        spray pyrolysis, atomization, etc.), wherein the particulate        comprises a single or a plurality of graphene-encapsulated        primary particles of an anode active material, having a size        from 5 nm to 20 μm, wherein the graphene-encapsulated primary        particle is composed of a primary particle of the anode active        material and multiple sheets of first graphene material        overlapped together to embrace or encapsulate the primary        particle and wherein the single or a plurality of        graphene-encapsulated primary particles, along with an optional        conductive additive, are further embraced or encapsulated by        multiple sheets of a second graphene material, wherein the first        graphene material is the same as or different from the second        graphene material, and wherein the first graphene and the second        graphene material is each in an amount from 0.01% to 20% by        weight and the optional conductive additive is in an amount from        0% to 50% by weight, all based on the total weight of the        particulate.

In certain specific embodiments, this invention provides aself-embracing or self-encapsulating method of first producinggraphene-embraced or graphene-encapsulated primary particles of an anodeactive material directly from a graphitic material. Some of thesegraphene-encapsulated particles are then clustered and packed togetherand further embraced by exterior graphene sheets. In an embodiment, themethod comprises:

-   -   a) mixing multiple particles of a graphitic material and        multiple primary particles of a solid anode active material,        plus optional ball-milling media, to form a mixture in an        impacting chamber of an energy impacting apparatus, wherein        preferably the graphitic material has never been intercalated,        oxidized, or exfoliated and does not include previously produced        isolated graphene sheets. In some embodiments, the impacting        chamber contains no ball-milling media (i.e., the solid        electrode active material particles themselves serve as an        impacting media and no externally added ball-milling media is        needed or involved);    -   b) operating the energy impacting apparatus with a frequency and        an intensity for a length of time sufficient for transferring        graphene sheets from the particles of graphitic material to        surfaces of the solid electrode active material particles to        produce a graphene-embraced electrode active material inside the        impacting chamber (i.e., solid electrode active material        particles impinge upon surfaces of graphitic material particles,        peeling off graphene sheets therefrom, and naturally allowing        the peeled-off graphene sheets to fully wrap around or embrace        the solid electrode active material particles);    -   c) recovering the graphene-embraced primary particles of anode        active material from the impacting chamber (this can be as        simple as removing the cap to the impacting chamber and removing        the particles of graphene-embraced electrode active material);        and    -   d) dispersing these graphene-embraced primary particles in a        liquid suspension containing additional graphene sheets        dispersed in a liquid medium (e.g. water, organic solvent,        alcohol, etc.) to form a slurry and then atomizing the slurry        into droplets (typically 1-100 μm in diameter) and removing the        liquid medium to form secondary particles.        The method further comprises a step of incorporating        particulates of graphene-embraced or graphene-encapsulated anode        active material into a battery electrode.

There can be some particles of graphitic material that are not fullyutilized (i.e., not all graphene sheets have been peeled off) after stepb). Hence, in an embodiment, an amount of residual graphitic materialremains after step b) and the method further comprises a step ofincorporating the graphene-embraced primary particles and the residualgraphitic material into secondary particles. The residual graphiticmaterial can serve as a conductive filler in the battery electrode.

In another embodiment, an amount of residual graphitic material remainsafter step b), and step c) includes a step of partially or completelyseparating the residual amount of graphitic material from thegraphene-embraced primary particles of electrode active material.

In some embodiments, the primary particles of solid electrode activematerial contain prelithiated or pre-sodiated particles. In other words,before the electrode active material primary particles (such as Si,SiO_(x), x=0.01-1.5, or SnO₂) are embraced by graphene sheets, theseparticles have been previously intercalated with Li or Na ions (e.g. viaelectrochemical charging) up to an amount of 0.1% to 30% by weight of Lior Na. This is a highly innovative and unique approach for the followingconsiderations. The intercalation of these particles with Li or Na hasallowed the Si, SiO_(x), or SnO₂ particles to expand to a large volume(potentially up to 380% of its original volume). If these prelithiatedor pre-sodiated particles are then wrapped around or embraced bygraphene sheets to form graphene-encapsulated primary particles, madeinto secondary particles, and incorporated into an electrode (i.e. anodecontaining graphene-embraced secondary particles of Si or SnO₂), theelectrode would no longer have any significant issues of electrodeexpansion and expansion-induced failure during subsequentcharge-discharge cycles of the lithium- or sodium-ion battery. In otherwords, the Si, SiO_(x), or or SnO₂ primary particles have been providedwith expansion space between these particles and the embracing graphenesheets. Our experimental data have surprisingly shown that this strategyleads to significantly longer battery cycle life and more efficientutilization of the electrode active material capacity.

In some embodiments, prior to the instant “graphene direct transfer andembracing process,” the particles of solid electrode active materialcontain particles pre-coated with a coating layer of a conductivematerial selected from carbon, pitch, carbonized resin, a conductivepolymer, a conductive organic material, a metal coating, a metal oxideshell, or a combination thereof. The coating layer thickness ispreferably in the range from 1 nm to 20 μm, preferably from 10 nm to 10μm, and further preferably from 100 nm to 1 μm.

In some embodiments, the primary particles of solid electrode activematerial contain particles that are pre-coated with a carbon precursormaterial selected from a coal tar pitch, petroleum pitch, mesophasepitch, polymer, organic material, or a combination thereof so that thecarbon precursor material resides between surfaces of the solidelectrode active material particles and the embracing graphene sheets,and the method further contains a step of heat-treating thegraphene-embraced electrode active material to convert the carbonprecursor material to a carbon material and pores, wherein the poresform empty spaces between surfaces of the solid electrode activematerial particles and the graphene sheets, and the carbon material iscoated on the surfaces of solid electrode active material particlesand/or chemically bonds the graphene sheets together.

In some embodiments, the primary particles of solid electrode activematerial contain particles pre-coated with a sacrificial materialselected from a metal, pitch, polymer, organic material, or acombination thereof in such a manner that the sacrificial materialresides between surfaces of particles of solid electrode active materialand the graphene sheets, and the method further contains a step ofpartially or completely removing the sacrificial material to form emptyspaces between surfaces of the solid electrode active material particlesand the graphene sheets.

In some embodiments, the method further comprises a step of exposing thegraphene-embraced primary particles of electrode active material to aliquid or vapor of a conductive material that is conductive to electronsand/or ions of lithium, sodium, magnesium, aluminum, or zinc.

In some embodiments, the electrode active material particles includepowder, flakes, beads, pellets, spheres, wires, fibers, filaments,discs, ribbons, or rods, having a diameter or thickness from 10 nm to 20μm. Preferably, the diameter or thickness is from 1 μm to 100 μm.

In the invented method, the graphitic material may be selected fromnatural graphite, synthetic graphite, highly oriented pyrolyticgraphite, graphite fiber, graphitic nanofiber, graphite fluoride,chemically modified graphite, mesocarbon microbead, partiallycrystalline graphite, or a combination thereof.

The method energy impacting apparatus may be a vibratory ball mill,planetary ball mill, high energy mill, basket mill, agitator ball mill,cryogenic ball mill, micro ball mill, tumbler ball mill, continuous ballmill, stirred ball mill, pressurized ball mill, plasma-assisted ballmill, freezer mill, vibratory sieve, bead mill, nanobead mill,ultrasonic homogenizer mill, centrifugal planetary mixer, vacuum ballmill, or resonant acoustic mixer. Optionally, milling media may be addedinto the impacting chamber and later removed upon completion of thegraphene-encapsulated primary particle production procedure.

The procedure of operating the energy impacting apparatus may beconducted in a continuous manner using a continuous energy impactingdevice

In the graphene-embraced electrode active material particles (theprimary particles or secondary particles), the graphene sheets of firstgraphene or second graphene material contain single-layer graphenesheets. In some embodiments, the graphene sheets contain at least 80%single-layer graphene or at least 80% few-layer graphene having nogreater than 10 graphene planes.

The impacting chamber may further contain a functionalizing agent andstep (b) of operating the energy impacting apparatus acts to chemicallyfunctionalize said graphene sheets with said functionalizing agent. Thefunctionalizing agent may contain a chemical functional group selectedfrom alkyl or aryl silane, alkyl or aralkyl group, hydroxyl group,carboxyl group, amine group, sulfonate group (—SO₃H), aldehydic group,quinoidal, fluorocarbon, or a combination thereof.

In some embodiments, the functionalizing agent contains an oxygenatedgroup selected from the group consisting of hydroxyl, peroxide, ether,keto, and aldehyde. In some embodiments, the functionalizing agentcontains a functional group selected from the group consisting of SO₃H,COOH, NH₂, OH, R′CHOH, CHO, CN, COCl, halide, COSH, SH, COOR′, SR′,SiR′₃, Si(—OR′—)_(y)R′₃-y, Si(—O—SiR′₂—)OR′, R″, Li, AlR′₂, Hg—X, TlZ₂and Mg—X; wherein y is an integer equal to or less than 3, R′ ishydrogen, alkyl, aryl, cycloalkyl, or aralkyl, cycloaryl, orpoly(alkylether), R″ is fluoroalkyl, fluoroaryl, fluorocycloalkyl,fluoroaralkyl or cycloaryl, X is halide, and Z is carboxylate ortrifluoroacetate, and combinations thereof.

In some embodiments, the functionalizing agent contains a functionalgroup is selected from the group consisting of amidoamines, polyamides,aliphatic amines, modified aliphatic amines, cycloaliphatic amines,aromatic amines, anhydrides, ketimines, diethylenetriamine (DETA),triethylene-tetramine (TETA), tetraethylene-pentamine (TEPA),polyethylene polyamine, polyamine epoxy adduct, phenolic hardener,non-brominated curing agent, non-amine curatives, and combinationsthereof.

The functionalizing agent may contain a functional group selected fromOY, NHY, O═C—OY, P═C—NR′Y, O═C—SY, O═C—Y, —CR′1-OY, N′Y or C′Y, and Y isa functional group of a protein, a peptide, an amino acid, an enzyme, anantibody, a nucleotide, an oligonucleotide, an antigen, or an enzymesubstrate, enzyme inhibitor or the transition state analog of an enzymesubstrate or is selected from R′—OH, R′—NR′₂, R′SH, R′CHO, R′CN, R′X,R′N+(R′)₃X, R′SiR′₃, R′Si(—OR′—)_(y)R′_(3-y), R′Si(—O—SiR′₂—) OR′,R′—R″, R′—N—CO, (C₂H₄O—)_(w)H, (—C₃H₆O—)_(w)H, (—C₂H₄O)_(w)—R′,(C₃H₆O)_(w)—R′, R′, and w is an integer greater than one and less than200.

The present invention also provides a mass of graphene-embracedsecondary particles of solid active material produced by theaforementioned method, wherein the graphene proportion is from 0.01% to20% by weight based on the total weight of graphene and solid activematerial particles combined.

Also provided is a battery electrode containing the graphene-embracedsecondary particles electrode active material produced according to thepresently invented method, and a battery containing such an electrode.The battery electrode containing the graphene-embraced secondaryparticles of electrode active material may be a lithium-ion battery,lithium metal secondary battery, lithium-sulfur battery, lithium-airbattery, lithium-selenium battery, sodium-ion battery, sodium metalsecondary battery, sodium-sulfur battery, sodium-air battery,magnesium-ion battery, magnesium metal battery, aluminum-ion battery,aluminum metal secondary battery, zinc-ion battery, zinc metal battery,or zinc-air battery.

The present invention provides several different configurations of abattery: (a) featuring a doubly graphene-protected anode (containinggraphene-embraced particulates of graphene-encapsulated primaryparticles), but more conventional cathode; (b) doubly graphene-protectedcathode, but more conventional anode; and (c) a doublygraphene-protected anode and a doubly graphene-protected cathode.

It may be noted that the graphene production step per se (peeling offgraphene sheets directly from graphite particles and immediately orconcurrently transferring these graphene sheets to electrode activematerial particle surfaces) is quite surprising, considering the factthat prior researchers and manufacturers have focused on more complex,time intensive and costly methods to create graphene in industrialquantities. In other words, it has been generally believed that chemicalintercalation and oxidation is needed to produce bulk quantities ofisolated graphene sheets (NGPs). The present invention defies thisexpectation in many ways:

-   -   1. Unlike the chemical intercalation and oxidation (which        requires expansion of inter-graphene spaces, further expansion        or exfoliation of graphene planes, and full separation of        exfoliated graphene sheets), the instant method directly removes        graphene sheets from a source graphitic material and transfers        these graphene sheets to surfaces of electrode active material        particles. No undesirable chemicals (e.g. sulfuric acid and        nitric acid) are used.    -   2. Unlike oxidation and intercalation, pristine graphene sheets        can be transferred onto the electrode active material. The        sheets being free of oxidation damage allow the creation of        graphene-encapsulated particle products with higher electrical        and thermal conductivity.    -   3. Contrary to common production methods, a washing process        requiring substantial amounts of water or solvent is not needed    -   4. Unlike bottom up production methods capable of producing        small graphene sheets, large graphene sheets can be produced        with the instant method.    -   5. Unlike CVD and solution-based metalorganic production        methods, elevated temperatures are not required to reduce        graphene oxide to graphene and metalorganic compounds to pure        metal. This greatly reduces the opportunity for undesirable        diffusion of carbon into the electrode active material.    -   6. Unlike CVD and solution-based metalorganic production        methods, this process is amenable to almost any electrode active        material. The electrode active material does not need to be a        compatible “template” or catalyst, as is required for the CVD        process.    -   7. This direct transfer process does not require the use of        externally added ball milling media (such as zirconia beads or        plastic beads). The electrode active material particles        themselves are the graphene-peeling media. The presence of extra        milling media is optional.    -   8. This method allows the creation of overlapping graphene        sheets, in some way analogous to fish scale, which slide over        one another when the primary particle expands or shrinks,        thereby preventing repeated direct exposure of the primary        particle surface and the solid-electrolyte interface (SEI)        coated thereon to the surrounding electrolyte and, hence,        eliminating repeated breakage and re-formation of SEI during        repeated charges/discharges. Presumably due to this main reason,        the battery cell containing secondary particles featuring such a        multi-level graphene protection strategy usually exhibit an        exceptionally long cycle life.    -   9. The present invention is amenable to industrial scale        production in a continuous energy impact device.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 A flow chart showing the most commonly used prior art process ofproducing highly oxidized graphene sheets (or nanographene platelets,NGPs) that entails tedious chemical oxidation/intercalation, rinsing,and high-temperature exfoliation procedures.

FIG. 2 A diagram showing the presently invented process for producinggraphene-embraced or graphene-encapsulated electrode active materialparticles via an energy impacting apparatus.

FIG. 3 A diagram showing the presently invented process for producinggraphene-embraced electrode active material particles via a continuousball mill.

FIG. 4 Charge-discharge cycling behaviors of 3 lithium cells featuringCo₃O₄ particle-based anodes: a) containing un-protected Co₃O₄ particles,b) graphene-encapsulated Co₃O₄ primary particles produced by the instantdirect transfer method; and c) graphene-embraced particulates (secondaryparticles) of graphene-encapsulated Co₃O₄ primary particles.

FIG. 5 Charge-discharge cycling behaviors of 3 lithium cells featuringSnO₂ particle-based anodes: the first containing un-protected SnO₂particles, second containing graphene-encapsulated primary SnO₂particles produced by the instant direct transfer method, and the thirdcontaining graphene-embraced particulates of graphene-encapsulatedprimary particles.

FIG. 6 Charge-discharge cycling behaviors of 3 lithium cells featuringmicron-scaled (3 μm) Si particle-based anodes: a) containingun-protected Si particles, b) graphene-embraced primary Si particlesproduced by the direct transfer method, and c) graphene-embracedparticulates of graphene-encapsulated Si particles produced by theinstant direct transfer method (Si particles themselves being thegraphene-peeling agent), followed by slurry spray-drying.

FIG. 7 Discharge capacity values (mAh/g, based on composite weight) of 3lithium cells featuring lithium iron phosphate (LFP) particle-basedcathodes, plotted as a function of discharge C-rates: first onecontaining un-protected LFO particles (mixed with 12% by weight carbon),second one containing graphene-encapsulated carbon-added LFP primaryparticles produced by the instant direct transfer method (4% graphene+8%C), and third one RGO-embraced particulates of graphene-encapsulatedprimary LFP particles. (1 C rate=complete discharge in 1 hour or 60minute; 5 C rate=complete discharge in 60/5=12 minutes; 0.1 Crate=complete discharge in 60/0.1=600 minutes or 10 hours)

FIG. 8 Charge-discharge cycling behaviors of 3 lithium cells featuringLiV₂O₅ nanorod-based cathodes: a) containing RGO-embraced particulatesof graphene-encapsulated LiV₂O₅ nanorods, b) graphene-embraced LiV₂O₅nanorods produced by the direct transfer method (approximately 5%graphene+7% C), and c) LiV₂O₅ nanorods protected by a carbon matrix.

FIG. 9(A) SEM image of a representative anode particulate;

FIG. 9(B) SEM image of a representative cathode particulate.

DETAILED DESCRIPTION OF PREFERRED EMBODIMENTS

Carbon materials can assume an essentially amorphous structure (glassycarbon), a highly organized crystal (graphite), or a whole range ofintermediate structures that are characterized in that variousproportions and sizes of graphite crystallites and defects are dispersedin an amorphous matrix. Typically, a graphite crystallite is composed ofa number of graphene sheets or basal planes that are bonded togetherthrough van der Waals forces in the c-axis direction, the directionperpendicular to the basal plane. These graphite crystallites aretypically micron- or nanometer-sized. The graphite crystallites aredispersed in or connected by crystal defects or an amorphous phase in agraphite particle, which can be a graphite flake, carbon/graphite fibersegment, carbon/graphite whisker, or carbon/graphite nanofiber. In otherwords, graphene planes (hexagonal lattice structure of carbon atoms)constitute a significant portion of a graphite particle.

One preferred specific embodiment of the present invention is a methodof peeling off graphene planes of carbon atoms (1-10 planes of atomsthat are single-layer or few-layer graphene sheets) that are directlytransferred to surfaces of electrode active material particles (theprimary particles). A graphene sheet or nanographene platelet (NGP) isessentially composed of a sheet of graphene plane or multiple sheets ofgraphene plane stacked and bonded together (typically, on an average,less than 10 sheets per multi-layer platelet). Each graphene plane, alsoreferred to as a graphene sheet or a hexagonal basal plane, comprises atwo-dimensional hexagonal structure of carbon atoms. Each platelet has alength and a width parallel to the graphite plane and a thicknessorthogonal to the graphite plane. By definition, the thickness of an NGPis 100 nanometers (nm) or smaller, with a single-sheet NGP being as thinas 0.34 nm. However, the NGPs produced with the instant methods aremostly single-layer graphene and some few-layer graphene sheets (<5layers). The length and width of a NGP are typically between 200 nm and20 μm, but could be longer or shorter, depending upon the sizes ofsource graphite material particles.

The present invention provides a strikingly simple, fast, scalable,environmentally benign, and cost-effective process that avoidsessentially all of the drawbacks associated with prior art processes ofproducing graphene sheets and obviates the need to execute a separate(additional) process to combine the produced graphene sheets andparticles of an electrode active material (anode or cathode activematerial) together to form a composite or hybrid electrode activematerial.

As schematically illustrated in FIG. 2, one preferred embodiment of thismethod entails placing particles of a source graphitic material andparticles of a solid electrode active material (without any externallyadded impacting balls, such as ball-milling media) in an impactingchamber. After loading, the resulting mixture is exposed to impactingenergy, which is accomplished, for instance, by rotating the chamber toenable the impacting of the active material particles against graphiteparticles. These repeated impacting events (occurring in highfrequencies and high intensity) act to peel off graphene sheets from thesurfaces of graphitic material particles and, immediately and directly,transfer these graphene sheets to the surfaces of the active materialparticles to form graphene-embraced active material particles.Typically, the entire particle is covered by graphene sheets (fullywrapped around, embraced or encapsulated). This is herein referred to asthe “direct transfer” process.

Alternatively but less desirably, impacting balls (e.g. stainless steelor zirconia beads) may be added into the impacting chambers and, assuch, graphene sheets may also be peeled off by the impacting balls andtentatively transferred to the surfaces of these impacting balls first.When the graphene-coated impacting balls subsequently impinge upon thesolid electrode active material particles, the graphene sheets aretransferred to surfaces of the electrode active material particles toform graphene-coated active material particles. This is an “indirecttransfer” process. A major drawback of such an indirect transfer processis the need to separate the externally added impacting balls (e.g.ball-milling media) from the graphene-embraced particles. This is notalways possible or economically feasible, however.

In less than two hours (often less than 1 hour) of operating the directtransfer process, most of the constituent graphene sheets of sourcegraphite particles are peeled off, forming mostly single-layer grapheneand few-layer graphene (less than 10 graphene planes; mostly less than 5layers or 5 graphene planes in the present study). Following the directtransfer process (graphene sheets wrapped around active materialparticles), the residual graphite particles (if present) are separatedfrom the graphene-embraced (graphene-encapsulated) particles using abroad array of methods. Separation or classification ofgraphene-embraced (graphene-encapsulated) particles from residualgraphite particles (if any) can be readily accomplished based on theirdifferences in weight or density, particle sizes, magnetic properties,etc. The resulting graphene-embraced particles are already atwo-component material; i.e. they are already “mixed” and there is noneed to have a separate process of mixing isolated graphene sheets withelectrode active material particles.

In other words, production of graphene sheets and coating of graphenesheets onto primary particle surfaces of electrode active materials areessentially accomplished concurrently in one operation. This is in starkcontrast to the traditional processes of producing graphene sheets firstand then subsequently mixing the graphene sheets with an activematerial. Traditional dry mixing typically does not result inhomogeneous mixing or dispersion of two or multiple components. It isalso challenging to properly disperse nanomaterials in a solvent to forma battery slurry mass for coating on a current collector, which is themost commonly used electrode production process for the lithium battery.

As shown in FIG. 1, the prior art chemical processes for producinggraphene sheets or platelets alone typically involve immersing graphitepowder in a mixture of concentrated sulfuric acid, nitric acid, and anoxidizer, such as potassium permanganate or sodium perchlorate, forminga reacting mass that requires typically 5-120 hours to complete thechemical intercalation/oxidation reaction. Once the reaction iscompleted, the slurry is subjected to repeated steps of rinsing andwashing with water and then subjected to drying treatments to removewater. The dried powder, referred to as graphite intercalation compound(GIC) or graphite oxide (GO), is then subjected to a thermal shocktreatment. This can be accomplished by placing GIC in a furnace pre-setat a temperature of typically 800-1100° C. (more typically 950-1050°C.). The resulting products are typically highly oxidized graphene (i.e.graphene oxide with a high oxygen content), which must be chemically orthermal reduced to obtain reduced graphene oxide (RGO). RGO is found tocontain a high defect population and, hence, is not as conducting aspristine graphene. We have observed that that the pristine graphenepaper (prepared by vacuum-assisted filtration of pristine graphenesheets, as herein prepared) exhibit electrical conductivity values inthe range from 1,500-4,500 S/cm. In contrast, the RGO paper prepared bythe same paper-making procedure typically exhibits electricalconductivity values in the range from 100-1,000 S/cm.

In the most common implementation of ball mill mixing, previouslyproduced graphene sheets or platelets are added to electrode activematerial powders. Impact energy is applied via ball mill for a period oftime to disperse graphene platelets or sheets in the powder. This isoften carried out in a liquid (solvent) solution. The disadvantages ofthis graphene/active material mixing process are obvious—graphene is acostly input material, solvent recovery is required, and mostsignificantly, the graphene input into the process has been damaged byoxidation during prior processing. This reduces desirable endproperties, such as thermal conductivity and electrical conductivity.

Another prior art process is coating of CVD onto metal nanoparticles.This is the most limited of all prior art methods, being possible onlyon certain metals that are suitable catalysts for facilitatingdecomposition of hydrocarbon gas to form carbon atoms and as templatesfor graphene to grow on. As a “bottom up” graphene production method, itrequires costly capital equipment and costly input materials.

In all these prior art processes for producing graphene-coated electrodeactive material particles, isolated graphene sheets and particles of theactive material are dispersed in a solvent (e.g. NMP) to form a slurry.The slurry is then dried (e.g. using spray drying) to formgraphene-active material composite particles. These composites do notnecessarily have the morphology or structure of active materialparticles being fully wrapped around or embraced.

In contrast, the presently invented impacting process entails combininggraphene production, functionalization (if desired), and mixing ofgraphene sheets with electrode active material particles in a singleoperation. This fast and environmentally benign process not only avoidssignificant chemical usage, but also produces embracing graphene sheetsof higher quality—pristine graphene as opposed to thermally reducedgraphene oxide produced by the prior art process. Pristine grapheneenables the creation of embraced particles with higher electrical andthermal conductivity.

Although the mechanisms remain incompletely understood, thisrevolutionary process of the present invention has essentiallyeliminated the conventionally required functions of graphene planeexpansion, intercalant penetration, exfoliation, and separation ofgraphene sheets and replace it with a single, entirely mechanicalexfoliation process. The whole process can take less than 2 hours(typically 10 minutes to 1 hour), and can be done with no addedchemicals. This is absolutely stunning, a shocking surprise to eventhose top scientists and engineers or those of extraordinary ability inthe art.

Another surprising result of the present study is the observation that awide variety of carbonaceous and graphitic materials can be directlyprocessed without any particle size reduction or pre-treatment. Theparticle size of graphite can be smaller than, comparable to, or largerthan the particle size of the electrode active material primaryparticles. The graphitic material may be selected from natural graphite,synthetic graphite, highly oriented pyrolytic graphite, mesocarbonmicrobead, graphite fiber, graphitic nanofiber, graphite oxide, graphitefluoride, chemically modified graphite, exfoliated graphite, or acombination thereof. It may be noted that the graphitic material usedfor the prior art chemical production and reduction of graphene oxiderequires size reduction to 75 um or less in average particle size. Thisprocess requires size reduction equipment (for example hammer mills orscreening mills), energy input, and dust mitigation. By contrast, theenergy impacting device method can accept almost any size of graphiticmaterial. A starting graphitic material of several mm or cm in size orlarger or a starting material as small as nanoscaled has beensuccessfully processed to create graphene-coated or graphene-embeddedparticles of cathode or anode active materials. The only size limitationis the chamber capacity of the energy impacting device; but this chambercan be very large (industry-scaled).

The presently invented process is capable of producing single-layergraphene sheets that completely wrap around the primary particles of anelectrode active material. In many examples, the graphene sheetsproduced contain at least 80% single-layer graphene sheets. The grapheneproduced can contain pristine graphene, oxidized graphene with less than5% oxygen content by weight, graphene fluoride, graphene oxide with lessthan 5% fluorine by weight, graphene with a carbon content of no lessthan 95% by weight, or functionalized graphene.

The presently invented process does not involve the production of GICand, hence, does not require the exfoliation of GIC at a highexfoliation temperature (e.g. 800-1,100° C.). This is another majoradvantage from environmental protection perspective. The prior artprocesses require the preparation of dried GICs containing sulfuric acidand nitric acid intentionally implemented in the inter-graphene spacesand, hence, necessarily involve the decomposition of H₂SO₄ and HNO₃ toproduce volatile gases (e.g. NO_(x) and SO_(N)) that are highlyregulated environmental hazards. The presently invented processcompletely obviates the need to decompose H₂SO₄ and HNO₃ and, hence, isenvironmentally benign. No undesirable gases are released into theatmosphere during the combined graphite expansion/exfoliation/separationprocess of the present invention.

In a desired embodiment, the presently invented method is carried out inan automated and/or continuous manner. For instance, as illustrated inFIG. 3, the mixture of graphite particles 1 and electrode activematerial particles 2 is delivered by a conveyer belt 3 and fed into acontinuous ball mill 4. After ball milling to form graphene-embracedparticles, the product mixture (possibly also containing some residualgraphite particles) is discharged from the ball mill apparatus 4 into ascreening device (e.g. a rotary drum 5) to separate graphene-embracedparticles from residual graphite particles (if any). This separationoperation may be assisted by a magnetic separator 6 if the electrodeactive material is ferromagnetic (e.g. containing Fe, Co, Ni, orMn-based metal in some desired electronic configuration). Thegraphene-embraced particles may be delivered into a powder classifier, acyclone, and or an electrostatic separator. The particles may be furtherprocessed, if so desired, by melting 7, pressing 8, orgrinding/pelletizing apparatus 9. These procedures can be fullyautomated. The process may include characterization or classification ofthe output material and recycling of insufficiently processed materialinto the continuous energy impacting device. The process may includeweight monitoring of the load in the continuous energy impacting deviceto optimize material properties and throughput.

The electrode active materials that are placed into the impactingchamber can be an anode active material or a cathode active material.For the anode active materials, those materials capable of storinglithium ions greater than 372 mAh/g (theoretical capacity of naturalgraphite) are particularly desirable. Examples of these high-capacityanode active materials are Si, Ge, Sn, SnO₂, Co₃O₄, etc. As discussedearlier, these materials, if implemented in the anode, have the tendencyto expand and contract when the battery is charged and discharged. Atthe electrode level, the expansion and contraction of the anode activematerial can lead to expansion and contraction of the anode, causingmechanical instability of the battery cell. At the anode active materiallevel, repeated expansion/contraction of particles of Si, SiO_(x), Ge,Sn, SnO₂, Co₃O₄, etc. quickly leads to pulverization of these particlesand rapid capacity decay of the electrode.

Thus, for the purpose of addressing these problems, the primaryparticles of solid electrode active material may be reduced to smallerthan 150 nm (more preferably <100 nm) in size and/or containprelithiated or pre-sodiated particles. The particle size reduction canaddress the particle pulverization problem. We have surprisinglyobserved that the low first-cycle efficiency and repeated SEIbreakage/re-formation problems can be at least partially overcome usingthe prelithiation strategy. The encapsulation of primary particles ofhigh-capacity anode materials (e.g. Si, SiO_(x), Ge, Sn, SnO₂, Co₃O₄,etc.) or high-capacity cathode materials (S, lithium polysulfide, etc.)with overlapping graphene sheets that are capable of sliding over oneanother enables the primary particles to expand and shrink withoutexposing the primary particles to the surrounding electrolyte can helpreduce the capacity decay problem.

Before the electrode active material particles (such as Si, Ge, Sn,SnO₂, SiO_(x), Co₃O₄, etc.) are embraced by graphene sheets, theseparticles may be previously intercalated with Li or Na ions (e.g. viaelectrochemical charging). This is a highly innovative and uniqueapproach based on the following considerations. The intercalation ofthese particles with Li or Na would allow these particles to expand to alarge volume or to its full capacity (potentially up to 380% of itsoriginal volume). If these prelithiated or pre-sodiated particles arethen wrapped around or fully embraced by graphene sheets andincorporated into an electrode (e.g. anode containing graphene-embracedSi or SnO₂ particles), the electrode would no longer have anysignificant issues of electrode expansion and expansion-induced failureduring subsequent charge-discharge cycles of the lithium- or sodium-ionbattery. In other words, the Si or SnO₂ particles have been expanded totheir maximum volume (during battery charging) and they can only shrink(during subsequent battery discharge). These contracted particles havebeen previously provided with expansion space between these particlesand the embracing graphene sheets. Our experimental data have shown thatthis strategy surprisingly leads to significantly longer battery cyclelife and better utilization of the electrode active material capacity.

In some embodiments, prior to the instant procedures of grapheneproduction, direct transfer and embracing process, the particles ofsolid electrode active material contain particles that are pre-coatedwith a coating of a conductive material selected from carbon, pitch,carbonized resin, a conductive polymer, a conductive organic material, ametal coating, a metal oxide shell, or a combination thereof. Thecoating layer thickness is preferably in the range from 1 nm to 10 μm,preferably from 10 nm to 1 μm, and further preferably from 20 nm to 200nm. This coating is implemented for the purpose of establishing asolid-electrolyte interface (SEI) to increase the useful cycle life of alithium-ion or sodium-ion battery.

In some embodiments, the primary particles of solid electrode activematerial contain particles that are pre-coated with a carbon precursormaterial selected from a coal tar pitch, petroleum pitch, mesophasepitch, polymer, organic material, or a combination thereof so that thecarbon precursor material resides between surfaces of the solidelectrode active material particles and the graphene sheets, and themethod further contains a step of heat-treating the graphene-embracedelectrode active material to convert the carbon precursor material to acarbon material and pores, wherein the pores form empty spaces betweensurfaces of the solid electrode active material particles and thegraphene sheets and the carbon material is coated on the surfaces ofsolid electrode active material particles and/or chemically bonds thegraphene sheets together. The carbon material helps to completely sealoff the embracing graphene sheets to prevent direct contact of theembraced anode active material with liquid electrolyte, which otherwisecontinues to form additional SEI via continuously consuming the lithiumions or solvent in the electrolyte, leading to rapid capacity decay.

In some embodiments, the primary particles of solid electrode activematerial contain particles pre-coated with a sacrificial materialselected from a metal, pitch, polymer, organic material, or acombination thereof in such a manner that the sacrificial materialresides between surfaces of solid electrode active material particlesand the graphene sheets, and the method further contains a step ofpartially or completely removing the sacrificial material to form emptyspaces between surfaces of the solid electrode active material particlesand the graphene sheets. The empty spaces can accommodate the expansionof embraced active material particles without breaking the embracedparticles.

In some embodiments, the method further comprises a step of exposing thegraphene-embraced electrode active material to a liquid or vapor of aconductive material that is conductive to electrons and/or ions oflithium, sodium, magnesium, aluminum, or zinc. This procedure serves toprovide a stable SEI or to make the SEI more stable.

The particles of electrode active material may be an anode activematerial selected from the group consisting of: (A) lithiated andun-lithiated silicon (Si), germanium (Ge), tin (Sn), lead (Pb), antimony(Sb), bismuth (Bi), zinc (Zn), aluminum (Al), titanium (Ti), nickel(Ni), cobalt (Co), and cadmium (Cd); (B) lithiated and un-lithiatedalloys or intermetallic compounds of Si, Ge, Sn, Pb, Sb, Bi, Zn, Al, Ti,Ni, Co, or Cd with other elements; (C) lithiated and un-lithiatedoxides, carbides, nitrides, sulfides, phosphides, selenides, andtellurides of Si, Ge, Sn, Pb, Sb, Bi, Zn, Al, Ti, Fe, Ni, Co, or Cd, andtheir mixtures, composites, or lithium-containing composites; (D)lithiated and un-lithiated salts and hydroxides of Sn; (E) lithiumtitanate, lithium manganate, lithium aluminate, lithium-containingtitanium oxide, lithium transition metal oxide; and combinationsthereof. Both sodiated and un-sodiated versions of the materials in theabove list are also anode active materials for sodium-ion batteries.

The electrode active material may be a cathode active material selectedfrom an inorganic material, an organic material, an intrinsicallyconducting polymer (known to be capable of string lithium ions), a metaloxide/phosphate/sulfide, or a combination thereof. The metaloxide/phosphate/sulfide may be selected from a lithium cobalt oxide,lithium nickel oxide, lithium manganese oxide, lithium vanadium oxide,lithium-mixed metal oxide, lithium iron phosphate, lithium manganesephosphate, lithium vanadium phosphate, lithium mixed metal phosphate,sodium cobalt oxide sodium nickel oxide, sodium manganese oxide, sodiumvanadium oxide, sodium-mixed metal oxide, sodium iron phosphate, sodiummanganese phosphate, sodium vanadium phosphate, sodium mixed metalphosphate, transition metal sulfide, lithium polysulfide, sodiumpolysulfide, magnesium polysulfide, or a combination thereof.

In some embodiments, the electrode active material may be a cathodeactive material selected from sulfur, sulfur compound, sulfur-carboncomposite, sulfur-polymer composite, lithium polysulfide, transitionmetal dichalcogenide, a transition metal trichalcogenide, or acombination thereof. The inorganic material may be selected from TiS₂,TaS₂, MoS₂, NbSe₃, MnO₂, COO₂, an iron oxide, a vanadium oxide, or acombination thereof. This group of materials is particularly suitablefor use as a cathode active material of a lithium metal battery.

The metal oxide/phosphate/sulfide contains a vanadium oxide selectedfrom the group consisting of VO₂, Li_(x)VO₂, V₂O₅, Li_(x)V₂O₅, V₃O₈,Li_(x)V₃O₈, Li_(x)V₃O₇, V₄O₉, Li_(x)V₄O₉, V₆O₁₃, Li_(x)V₆O₁₃, theirdoped versions, their derivatives, and combinations thereof, wherein0.1<x<5. In some embodiments, the metal oxide/phosphate/sulfide isselected from a layered compound LiMO₂, spinel compound LiM₂O₄, olivinecompound LiMPO₄, silicate compound Li₂MSiO₄, Tavorite compound LiMPO₄F,borate compound LiMBO₃, or a combination thereof, wherein M is atransition metal or a mixture of multiple transition metals.

The inorganic material may be selected from: (a) bismuth selenide orbismuth telluride, (b) transition metal dichalcogenide ortrichalcogenide, (c) sulfide, selenide, or telluride of niobium,zirconium, molybdenum, hafnium, tantalum, tungsten, titanium, cobalt,manganese, iron, nickel, or a transition metal; (d) boron nitride, or(e) a combination thereof.

The organic material or polymeric material may be selected fromPoly(anthraquinonyl sulfide) (PAQS), a lithium oxocarbon,3,4,9,10-perylenetetracarboxylic dianhydride (PTCDA),poly(anthraquinonyl sulfide), pyrene-4,5,9,10-tetraone (PYT),polymer-bound PYT, Quino(triazene), redox-active organic material,Tetracyanoquinodimethane (TCNQ), tetracyanoethylene (TCNE),2,3,6,7,10,11-hexamethoxytriphenylene (HMTP), poly(5-amino-1,4-dyhydroxyanthraquinone) (PADAQ), phosphazene disulfide polymer ([(NPS₂)₃]n),lithiated 1,4,5,8-naphthalenetetraol formaldehyde polymer,Hexaazatrinaphtylene (HATN), Hexaazatriphenylene hexacarbonitrile(HAT(CN)₆), 5-Benzylidene hydantoin, Isatine lithium salt, Pyromelliticdiimide lithium salt, tetrahydroxy-p-benzoquinone derivatives (THQLi₄),N,N′-diphenyl-2,3,5,6-tetraketopiperazine (PHP),N,N′-diallyl-2,3,5,6-tetraketopiperazine (AP),N,N′-dipropyl-2,3,5,6-tetraketopiperazine (PRP), a thioether polymer, aquinone compound, 1,4-benzoquinone, 5,7,12,14-pentacenetetrone (PT),5-amino-2,3-dihydro-1,4-dyhydroxy anthraquinone (ADDAQ),5-amino-1,4-dyhydroxy anthraquinone (ADAQ), calixquinone, Li₄C₆O₆,Li₂C₆O₆, Li₆C₆O₆, or a combination thereof. These compounds arepreferably mixed with a conducting material to improve their electricalconductivity, rigidity and strength so as to enable the peeling-off ofgraphene sheets from the graphitic material particles.

The thioether polymer in the above list may be selected fromPoly[methanetetryl-tetra(thiomethylene)] (PMTTM),Poly(2,4-dithiopentanylene) (PDTP), a polymer containingPoly(ethene-1,1,2,2-tetrathiol) (PETT) as a main-chain thioetherpolymers, a side-chain thioether polymer having a main-chain consistingof conjugating aromatic moieties, and having a thioether side chain as apendant, Poly(2-phenyl-1,3-dithiolane) (PPDT),Poly(1,4-di(1,3-dithiolan-2-yl)benzene) (PDDTB),poly(tetrahydrobenzodithiophene) (PTHBDT),poly[1,2,4,5-tetrakis(propylthio)benzene] (PTKPTB, orpoly[3,4(ethylenedithio)thiophene] (PEDTT).

In some embodiments, the organic material contains a phthalocyaninecompound selected from copper phthalocyanine, zinc phthalocyanine, tinphthalocyanine, iron phthalocyanine, lead phthalocyanine, nickelphthalocyanine, vanadyl phthalocyanine, fluorochromium phthalocyanine,magnesium phthalocyanine, manganous phthalocyanine, dilithiumphthalocyanine, aluminum phthalocyanine chloride, cadmiumphthalocyanine, chlorogallium phthalocyanine, cobalt phthalocyanine,silver phthalocyanine, a metal-free phthalocyanine, a chemicalderivative thereof, or a combination thereof. These compounds arepreferably mixed with a conducting material to improve their electricalconductivity and rigidity so as to enable the peeling-off of graphenesheets from the graphitic material particles.

In some embodiments, the electrode active material particles includepowder, flakes, beads, pellets, spheres, wires, fibers, filaments,discs, ribbons, or rods, having a diameter or thickness from 10 nm to 20μm. Preferably, the diameter or thickness is from 1 m to 100 km.

In the invented method, the graphitic material may be selected fromnatural graphite, synthetic graphite, highly oriented pyrolyticgraphite, graphite fiber, graphitic nanofiber, graphite fluoride,chemically modified graphite, mesocarbon microbead, partiallycrystalline graphite, or a combination thereof.

The energy impacting apparatus may be a vibratory ball mill, planetaryball mill, high energy mill, basket mill, agitator ball mill, cryogenicball mill, micro ball mill, tumbler ball mill, continuous ball mill,stirred ball mill, pressurized ball mill, plasma-assisted ball mill,freezer mill, vibratory sieve, bead mill, nanobead mill, ultrasonichomogenizer mill, centrifugal planetary mixer, vacuum ball mill, orresonant acoustic mixer. The procedure of operating the energy impactingapparatus may be conducted in a continuous manner using a continuousenergy impacting device

Graphene sheets transferred to electrode active material surfaces have asignificant proportion of surfaces that correspond to the edge planes ofgraphite crystals. The carbon atoms at the edge planes are reactive andmust contain some heteroatom or group to satisfy carbon valency. Thereare many types of functional groups (e.g. hydroxyl and carboxylic) thatare naturally present at the edge or surface of graphene nanoplateletsproduced through transfer to a solid carrier particle. Theimpact-induced kinetic energy is of sufficient energy and intensity tochemically activate the edges and even surfaces of graphene sheetsembraced around active material particles (e.g. creating highly activesites or free radicals). Provided that certain chemical speciescontaining desired chemical function groups (e.g. OH—, —COOH, —NH₂, Br—,etc.) are included in the impacting chamber, these functional groups canbe imparted to graphene edges and/or surfaces. In other words,production and chemical functionalization of graphene sheets can beaccomplished concurrently by including appropriate chemical compounds inthe impacting chamber. In summary, a major advantage of the presentinvention over other processes is the simplicity of simultaneousproduction and modification of graphene surface chemistry for improvedbattery performance.

Graphene platelets derived by this process may be functionalized throughthe inclusion of various chemical species in the impacting chamber. Ineach group of chemical species discussed below, we selected 2 or 3chemical species for functionalization studies.

In one preferred group of chemical agents, the resulting functionalizedNGP may broadly have the following formula(e): [NGP]—R_(m), wherein m isthe number of different functional group types (typically between 1 and5), R is selected from SO₃H, COOH, NH₂, OH, R′CHOH, CHO, CN, COCl,halide, COSH, SH, COOR′, SR′, SiR′₃, Si(—OR′—)_(y)R′₃-y,Si(—O—SiR′₂—)OR′, R″, Li, AlR′₂, Hg—X, TlZ₂ and Mg—X; wherein y is aninteger equal to or less than 3, R′ is hydrogen, alkyl, aryl,cycloalkyl, or aralkyl, cycloaryl, or poly(alkylether), R″ isfluoroalkyl, fluoroaryl, fluorocycloalkyl, fluoroaralkyl or cycloaryl, Xis halide, and Z is carboxylate or trifluoroacetate.

Graphene-embraced electrode active material particles may be used toimprove the mechanical properties, electrical conductivity and thermalconductivity of an electrode. For enhanced lithium-capturing and storingcapability, the functional group —NH₂ and —OH are of particularinterest. For example, diethylenetriamine (DETA) has three —NH₂ groups.If DETA is included in the impacting chamber, one of the three —NH₂groups may be bonded to the edge or surface of a graphene sheet and theremaining two un-reacted —NH₂ groups will be available for reversiblycapturing a lithium or sodium atom and forming a redox pair therewith.Such an arrangement provides an additional mechanism for storing lithiumor sodium ions in a battery electrode.

Other useful chemical functional groups or reactive molecules may beselected from the group consisting of amidoamines, polyamides, aliphaticamines, modified aliphatic amines, cycloaliphatic amines, aromaticamines, anhydrides, ketimines, diethylenetriamine (DETA),triethylene-tetramine (TETA), tetraethylene-pentamine (TEPA),hexamethylenetetramine, polyethylene polyamine, polyamine epoxy adduct,phenolic hardener, non-brominated curing agent, non-amine curatives, andcombinations thereof. These functional groups are multi-functional, withthe capability of reacting with at least two chemical species from atleast two ends. Most importantly, they are capable of bonding to theedge or surface of graphene using one of their ends and, duringsubsequent epoxy curing stage, are able to react with epoxide or epoxyresin material at one or two other ends.

The above-described [NGP]—R_(m) may be further functionalized. This canbe conducted by opening up the lid of an impacting chamber after the—R_(m) groups have been attached to graphene sheets and then adding thenew functionalizing agents to the impacting chamber and resuming theimpacting operation. The resulting graphene sheets or platelets includecompositions of the formula: [NGP]-A_(m), where A is selected from OY,NHY, O═C—OY, P═C—NR′Y, O═C—SY, O═C—Y, —CR′1-OY, N′Y or C′Y, and Y is anappropriate functional group of a protein, a peptide, an amino acid, anenzyme, an antibody, a nucleotide, an oligonucleotide, an antigen, or anenzyme substrate, enzyme inhibitor or the transition state analog of anenzyme substrate or is selected from R′—OH, R′—NR′₂, R′SH, R′CHO, R′CN,R′X, R′N+(R′)₃X, R′SiR′₃, R′Si(—OR′—)_(y)R′_(3-y), R′Si(—O—SiR′₂—)OR′,R′—R″, R′—N—CO, (C₂H₄O—)_(w)H, (—C₃H₆O—)_(w)H, (—C₂H₄O)_(w)—R′,(C₃H₆O)_(w)—R′, R′, and w is an integer greater than one and less than200.

The NGPs may also be functionalized to produce compositions having theformula: [NGP]—[R′-A]_(m), where m, R′ and A are as defined above. Thecompositions of the invention also include NGPs upon which certaincyclic compounds are adsorbed. These include compositions of matter ofthe formula: [NGP]—[X—R_(a)]_(m), where a is zero or a number less than10, X is a polynuclear aromatic, polyheteronuclear aromatic ormetallopolyheteronuclear aromatic moiety and R is as defined above.Preferred cyclic compounds are planar. More preferred cyclic compoundsfor adsorption are porphyrins and phthalocyanines. The adsorbed cycliccompounds may be functionalized. Such compositions include compounds ofthe formula, [NGP]—[X-A_(a)]_(m), where m, a, X and A are as definedabove.

The functionalized NGPs of the instant invention can be prepared bysulfonation, electrophilic addition to deoxygenated platelet surfaces,or metallation. The graphitic platelets can be processed prior to beingcontacted with a functionalizing agent. Such processing may includedispersing the platelets in a solvent. In some instances the plateletsmay then be filtered and dried prior to contact. One particularly usefultype of functional group is the carboxylic acid moieties, whichnaturally exist on the surfaces of NGPs if they are prepared from theacid intercalation route discussed earlier. If carboxylic acidfunctionalization is needed, the NGPs may be subjected to chlorate,nitric acid, or ammonium persulfate oxidation.

Carboxylic acid functionalized graphitic platelets are particularlyuseful because they can serve as the starting point for preparing othertypes of functionalized NGPs. For example, alcohols or amides can beeasily linked to the acid to give stable esters or amides. If thealcohol or amine is part of a di- or poly-functional molecule, thenlinkage through the O- or NH-leaves the other functionalities as pendantgroups. These reactions can be carried out using any of the methodsdeveloped for esterifying or aminating carboxylic acids with alcohols oramines as known in the art. Examples of these methods can be found in G.W. Anderson, et al., J. Amer. Chem. Soc. 96, 1839 (1965), which ishereby incorporated by reference in its entirety. Amino groups can beintroduced directly onto graphitic platelets by treating the plateletswith nitric acid and sulfuric acid to obtain nitrated platelets, thenchemically reducing the nitrated form with a reducing agent, such assodium dithionite, to obtain amino-functionalized platelets.Functionalization of the graphene-coated inorganic particles may be usedas a method to introduce dopants into the electrode active material.

The graphene-encapsulated primary particles of the anode activematerial, containing first graphene material attached with or without achemical functional group, along with sheets of a second graphenematerial, can be readily dispersed in a broad array of liquid mediums,such as water, alcohol, and organic solvent. For the preparation ofgraphene-protected particulates or secondary particles, multiplegraphene-encapsulated primary particles, optional conductive additive,and graphene sheets of the second graphene material are dispersed in adesired liquid medium to form a suspension or slurry. This suspension orslurry may be made into secondary particles by drying the suspension orslurry in a controlled manner, allowing the graphene-encapsulatedprimary particles, optional conductive additive, and the graphene sheetsof second graphene type to self-assemble into secondary particles orparticulates wherein the graphene-encapsulated primary particles, alongwith optional conductive additive, are clustered together to form aparticulate entity which is embraced by multiple sheets of the secondgraphene material. The particulates are typically substantiallyspherical or ellipsoidal in shape (e.g. FIGS. 9A) and 9(B).

These exterior graphene sheets (the second graphene material) may be thesame as or different than the first graphene material. In a preferredembodiment, the first graphene material is a pristine material (havinghighest electrical conductivity) and the second graphene material is agraphene oxide (having good self-assembling capability).

The step of drying the multi-component suspension to form the secondaryparticles is most preferably conducted using a spray-drying,spray-pyrolysis, or fluidized-bed drying procedure, or any procedurethat involves an atomization or aerosolizing step.

The following examples serve to provide the best modes of practice forthe present invention and should not be construed as limiting the scopeof the invention:

EXAMPLE 1 Graphene Embraced Particles of Electrode Active Materials

Several types of electrode active materials (both anode and cathodeactive materials) in a fine powder form were investigated. These includeCo₃O₄, Si, LiCoO₂, LiMn₂O₄, lithium Nickel Cobalt Manganese Oxide (NCM),lithium Nickel Cobalt Aluminum Oxide (NCA), lithium iron phosphate,etc., which are used as examples to illustrate the best mode ofpractice. These active materials either were prepared in house or werecommercially available.

In a typical experiment, 1 kg of electrode active material powder and100 grams of natural flake graphite, 50 mesh (average particle size 0.18mm; Asbury Carbons, Asbury N.J.) were placed in a high-energy ball millcontainer. The ball mill was operated at 300 rpm for 0.5 to 4 hours. Thecontainer lid was then removed and particles of the active materialswere found to be fully coated (embraced or encapsulated) with a darklayer, which was verified to be graphene by Raman spectroscopy. The massof processed material was placed over a 50 mesh sieve and, in somecases, a small amount of unprocessed flake graphite was removed.

These graphene-encapsulated primary particles were then dispersed in agraphene oxide (GO)/water suspension to obtain slurries having a solidcontent from approximately 0.5% to 20%. These slurries were thenspray-dried to prepare secondary particles or particulates containingclusters of pristine graphene-encapsulated primary particles that areembraced with GO sheets. These particulates were thermally reduced at300-700° C. under a H₂/N₂ flowing condition.

EXAMPLE 2 Functionalized Graphene-Encapsulated Sn Particles

The process of example 1 was replicated with the inclusion of 50 gramsof urea as a nitrogen source. The coated powder created wasfunctionalized graphene-encapsulated Sn, and multiple functionalizedgraphene-encapsulated particles were further embraced with reduced GOsheets prior to being incorporated as an anode active material in alithium-ion battery. It may be noted that chemical functionalization isused to improve wettability of the encapsulated primary particles tofacilitate self-assembling graphene-embraced particulates.

EXAMPLE 3 Graphene-Embraced SnO₂ Particles and Selected CathodeParticles (NCM)

In an experiment, 2 grams of 99.9% purity tin oxide powder (90 nmdiameter) and 0.25 grams highly oriented pyrolytic graphite (HOPG) wereplaced in a resonant acoustic mill and processed for 5 minutes. Forcomparison, the same experiment was conducted, but the milling containerfurther contains zirconia milling beads. We were surprised to discoverthat the former process (tin oxide particles serving as the millingmedia per se without the externally added zirconia milling beads) led tomostly single-particle particulate (each particulate contains oneparticle encapsulated by graphene sheets). In contrast, with thepresence of externally added milling beads, a graphene-embracedparticulate tends to contain multiple tin oxide particles (typically3-50) wrapped around by graphene sheets. These same results were alsoobserved for most of metal oxide-based electrode active materials (bothanode and cathode). We have further observed that encapsulatedsingle-particle particulates can be more easily made into secondgraphene material sheet-embraced particulates having the most desiredsecondary particle sizes (i.e. from 5 μm to 20 μm in diameter). Alsofirst graphene material-encapsulated single primary particles tend tolead to a higher specific capacity (especially under high-rateconditions) and longer battery longer cycle life as compared to multipleprimary particles encapsulated by graphene sheets of the first graphenematerial. The former particulates have the advantage that practicallyevery primary particle is embraced by a highly conducting graphenematerial and, as such, there is essentially no disruption ofelectron-conducting pathways in the resulting electrode (anode orcathode electrode).

EXAMPLE 4 Graphene-Encapsulated Si Micron Particles

In a first experiment, 500 g of Si powder (particle diameter˜3 μm) and50 grams of highly oriented pyrolytic graphite (HOPG) were placed in ahigh-intensity ball mill. The mill was operated for 20 minutes, afterwhich the container lid was opened and un-processed HOPG was removed bya 50 mesh sieve. The Si powder was coated with a dark layer, which wasverified to be graphene by Raman spectroscopy.

In a second experiment, micron-scaled Si particles from the same batchwere pre-coated with a layer of phenolic resin using amicro-encapsulation method that includes preparing solution of phenolicresin monomers, dispersing Si particles in this solution to form aslurry, and spry-drying the slurry to form resin-encapsulated Siparticles. The coated resin was then cured. Then, 500 g ofresin-encapsulated Si particles and 50 grams of HOPG were placed in ahigh-intensity ball mill. The mill was operated for 20 minutes, afterwhich the container lid was opened and un-processed HOPG was removed bya 50 mesh sieve. The resin-encapsulated Si particles (resin layer variedfrom 0.5 to 3.5 μm) were now also embraced with graphene sheets. Thesegraphene-embraced resin-encapsulated particles were then subjected to aheat treatment (up to 600° C.) that converted cure phenolic resin tocarbon. The converted carbon was mostly deposited on the exteriorsurface of the Si particles, leaving behind a gap or pores between theSi particle surface and the encapsulating graphene shell. This gapprovides room to accommodate the volume expansion of the Si particlewhen the lithium-ion battery is charged. Such a strategy leads tosignificantly improved battery cycle life.

In a third experiment, the Si particles were subjected toelectrochemical prelithiation to prepare several samples containing from5% to 54% Li. Prelithiation of an electrode active material means thematerial is intercalated or loaded with lithium before a battery cell ismade. Various prelithiated Si particles (primary particles) were thensubjected to the presently invented graphene encapsulation treatment,followed by particulate formation. The resulting graphene-encapsulatedprelithiated Si particles, further embraced by second type of graphenesheets, were incorporated as an anode active material in severallithium-ion cells.

EXAMPLE 5 Graphene-Embraced Ge Particles (Using Mesocarbon Microbeads orMCMBs as the Graphene Source)

In one example, 500 grams of B-doped Ge powder (anode active material)and 10 grams of MCMBs (China Steel Chemical Co., Taiwan) were placed ina ball mill, and processed for 3 hours. In separate experiments,un-processed MCMB was removed by sieving, air classification, andsettling in a solvent solution. The graphene loading of the coatedparticles was estimated to be 1.4 weight %. The graphene-encapsulated Geprimary particles were then made into secondary particles usingultrasonic spraying of slurries containing encapsulated Ge primaryparticles and GO and graphene fluoride sheets, respectively.

EXAMPLE 6 Graphene Encapsulation Via Direct Transfer Vs. ChemicalProduction of Graphene Sheets Plus Freezer Milling

A sample of graphene-embraced lithium titanate particles was preparedvia the presently invented direct transfer method (using lithiumtitanate particles themselves as the milling media and natural graphiteas the graphene source).

In a separate experiment, 10 grams of lithium titanate powder and 1 gramof reduced graphene oxide sheets (produced with the Hummer's methodexplained below) were placed in a freezer mill (Spex Mill, Spex SamplePrep, Metuchen N.J.) and processed for 10 minutes. In this experiment,graphite oxide as prepared by oxidation of graphite flakes with sulfuricacid, nitrate, and permanganate according to the method of Hummers [U.S.Pat. No. 2,798,878, Jul. 9, 1957]. Upon completion of the reaction, themixture was poured into deionized water and filtered. The graphite oxidewas repeatedly washed in a 5% solution of HCl to remove the majority ofthe sulfate ions. The sample was then washed repeatedly with deionizedwater until the pH of the filtrate was neutral. The slurry wasspray-dried and placed in a vacuum oven at 60° C. for 24 hours. Theinterlayer spacing of the resulting laminar graphite oxide wasdetermined by the Debey-Scherrer X-ray technique to be approximately0.73 nm (7.3 A). A sample of this material was subsequently transferredto a furnace pre-set at 650° C. for 4 minutes for exfoliation and heatedin an inert atmosphere furnace at 1200° C. for 4 hours to create a lowdensity powder comprised of few layer reduced graphene oxide (RGO).Surface area was measured via nitrogen adsorption BET.

As discussed in the Background section, there are seven (7) majorproblems associated with the chemical method of graphene production. Inaddition, the graphene sheets, once produced, tend to result in theformation of multiple-particle particulates that each contains aplurality of electrode active material particles embraced orencapsulated by graphene sheets. They appear to be incapable ofencapsulating a single particle.

EXAMPLE 7 Graphene-Encapsulated Lithium Iron Phosphate (LFP) as aCathode Active Material for a Lithium Metal Battery

LFP powder, un-coated or carbon-coated, is commercially available fromseveral sources. The carbon-coated LFP powder and un-coated LFP powdersamples were separately mixed with natural graphite particles in ballmill pots of a high-intensity ball mill apparatus. The apparatus wasoperated for 0.5 to 4 hours for each LFP material to producegraphene-encapsulated LFP particles.

Coated primary LFP particles were then made into secondary particlesaccording to similar procedures described in Example 1.

EXAMPLE 8 Graphene-Encapsulated V₂O₅ as an Example of a Transition MetalOxide Cathode Active Material of a Lithium Battery

V₂O₅ powder is commercially available. A mixture of V₂O₅ powder andnatural graphite (10/1 weight ratio) was sealed in each of 4 ballmilling pots symmetrically positioned in a high-intensity ball mill. Themill was operated for 1 hour to produce particulates ofgraphene-encapsulated V₂O₅ particles, which were implemented as thecathode active material in a lithium metal battery. Coated primaryparticles, 2-7.5% by weight pristine graphene or amine-functionalizedgraphene sheets, and a small amount of surfactant (Triton-100) wereadded into deionized water to make slurries. The slurries were thenultrasonic sprayed onto glass substrate surface to form particulates.

EXAMPLE 9 LiCoO₂ as an Example of Lithium Transition Metal Oxide CathodeActive Material for a Lithium-Ion Battery

In a set of experiments, a mixture of LiCoO₂ powder and natural graphite(100/1-10/1 weight ratio) was sealed in each of 4 ball milling potssymmetrically positioned in a high-intensity ball mill. The mill wasoperated for 0.5-4 hours to produce particulates ofgraphene-encapsulated LiCoO₂ particles. Coated primary particles werethen made into secondary particles according to similar proceduresdescribed in Example 1.

EXAMPLE 10 Organic Material (Li₂C₆O₆) as a Cathode Active Material of aLithium Metal Battery

The experiments associated with this example were conducted to determineif organic materials, such as Li₂C₆O₆, can be encapsulated in graphenesheets using the presently invented direct transfer method. The resultis that organic active materials alone are typically incapable ofpeeling off graphene sheets from graphite particles. However, if asecond active material (i.e. rigid particles of an inorganic material ora metal oxide/phosphate/sulfide) is implemented along with an organicactive material in a ball milling pot, then the organic materialparticles and inorganic material particles can be separately orconcurrently encapsulated to form graphene-encapsulated organicparticles, graphene-encapsulated inorganic particles, andgraphene-encapsulated mixture of organic and inorganic particles. Thisis interesting and surprising.

In order to synthesize dilithium rhodizonate (Li₂C₆O₆), the rhodizonicacid dihydrate (species 1 in the following scheme) was used as aprecursor. A basic lithium salt, Li₂CO₃ can be used in aqueous media toneutralize both enediolic acid functions. Strictly stoichiometricquantities of both reactants, rhodizonic acid and lithium carbonate,were allowed to react for 10 hours to achieve a yield of 90%. Dilithiumrhodizonate (species 2) was readily soluble even in a small amount ofwater, implying that water molecules are present in species 2. Water wasremoved in a vacuum at 180° C. for 3 hours to obtain the anhydrousversion (species 3).

A mixture of an organic cathode active material (Li₂C₆O₆) and aninorganic cathode active material (V₂O₅ and MoS₂, separately) wasball-milled for 0.5-2.0 hours to obtain a mixture ofgraphene-encapsulated particles.

Coated primary particles, 2-7.5% by weight pristine graphene oramine-functionalized graphene sheets, and a small amount of surfactant(Triton-100) were added into deionized water to make slurries. Theslurries were then ultrasonic sprayed onto glass substrate surface toform particulates.

It may be noted that the two Li atoms in the formula Li₂C₆O₆ are part ofthe fixed structure and they do not participate in reversible lithiumion storing and releasing. This implies that lithium ions must come fromthe anode side. Hence, there must be a lithium source (e.g. lithiummetal or lithium metal alloy) at the anode. In one battery cell hereintested, the anode current collector (Cu foil) is deposited with a layerof lithium (via sputtering). The resulting cell is a lithium metal cell.

EXAMPLE 11 Graphene-Encapsulated Na₃V₂(PO₄)₃/C and Na₃V₂(PO₄)₃ Cathodesfor Sodium Metal Batteries

The Na₃V₂(PO₄)₃/C sample was synthesized by a solid state reactionaccording to the following procedure: a stoichiometric mixture ofNaH₂PO₄.2H₂O (99.9%, Alpha) and V₂O₃ (99.9%, Alpha) powders was put inan agate jar as a precursor and then the precursor was ball-milled in aplanetary ball mill at 400 rpm in a stainless steel vessel for 8 h.During ball milling, for the carbon coated sample, sugar (99.9%, Alpha)was also added as the carbon precursor and the reductive agent, whichprevents the oxidation of V3⁺. After ball milling, the mixture washeated at 900° C. for 24 h in Ar atmosphere. Separately, the Na₃V₂(PO₄)₃powder was prepared in a similar manner, but without sugar. Samples ofboth powders were then subjected to ball milling in the presence ofnatural graphite particles to prepare graphene-encapsulated Na₃V₂(PO₄)₃particles and graphene-encapsulated carbon-coated Na₃V₂(PO₄)₃ particles.Coated primary particles, 5-13.5% by weight pristine graphene oramine-functionalized graphene sheets, and a small amount of surfactant(Triton-100) were added into deionized water to make slurries. Theslurries were then spray-dried to form particulates.

The particulates of cathode active materials were used in several Nametal cells containing 1 M of NaPF₆ salt in PC+DOL as the electrolyte.It was discovered that graphene encapsulation significantly improved thecycle stability of all Na metal cells studied. In terms of cycle life,the following sequence was observed: graphene-encapsulatedNa₃V₂(PO₄)₃/C>graphene-encapsulatedNa₃V₂(PO₄)₃>Na₃V₂(PO₄)₃/C>Na₃V₂(PO₄)₃.

EXAMPLE 12 Preparation of Graphene-Encapsulated MoS₂ Particles as aCathode Active Material of a Na Metal Battery

A wide variety of inorganic materials were investigated in this example.For instance, an ultra-thin MoS₂ material was synthesized by a one-stepsolvothermal reaction of (NH₄)₂MoS₄ and hydrazine in N,N-dimethylformamide (DMF) at 200° C. In a typical procedure, 22 mg of(NH₄)₂MoS₄ was added to 10 ml of DMF. The mixture was sonicated at roomtemperature for approximately 10 min until a clear and homogeneoussolution was obtained. After that, 0.1 ml of N₂H₄.H₂O was added. Thereaction solution was further sonicated for 30 min before beingtransferred to a 40 mL Teflon-lined autoclave. The system was heated inan oven at 200° C. for 10 h. Product was collected by centrifugation at8000 rpm for 5 min, washed with DI water and recollected bycentrifugation. The washing step was repeated for 5 times to ensure thatmost DMF was removed.

Subsequently, MoS₂ particles were dried and subjected to grapheneencapsulation by high-intensity ball milling in the presence of naturalgraphite particles. Coated primary particles were then made intosecondary particles according to similar procedures described in Example1.

EXAMPLE 13 Preparation of Two-Dimensional (2D) Layered Bi₂Se₃Chalcogenide Nanoribbons

The preparation of (2D) layered Bi₂Se₃ chalcogenide nanoribbons iswell-known in the art. In the present study, Bi₂Se₃ nanoribbons weregrown using the vapor-liquid-solid (VLS) method. Nanoribbons hereinproduced are, on average, 30-55 nm thick with widths and lengths rangingfrom hundreds of nanometers to several micrometers. Larger nanoribbonswere subjected to ball-milling for reducing the lateral dimensions(length and width) to below 200 nm. Nanoribbons prepared by theseprocedures were subjected to graphene encapsulation using the presentlyinvented direct transfer method. Coated primary particles were then madeinto secondary particles according to similar procedures described inExample 1.

The graphene double-encapsulated Bi₂Se₃ nanoribbons were used as acathode active material for Na battery. Surprisingly, Bi₂Se₃chalcogenide nanoribbons are capable of storing Na ions on theirsurfaces.

EXAMPLE 14 Preparation of Graphene-Encapsulated MnO₂ and NaMnO₂ CathodeActive Material for Na Metal Cells and Zn Metal Cells

For the preparation of the MnO₂ powder, a 0.1 mol/L KMnO₄ aqueoussolution was prepared by dissolving potassium permanganate in deionizedwater. Meanwhile, 13.32 g surfactant of high purity sodiumbis(2-ethylhexyl) sulfosuccinate was added in 300 mL iso-octane (oil)and stirred well to get an optically transparent solution. Then, 32.4 mLof 0.1 mol/L KMnO₄ solution was added into the solution, which wasultrasonicated for 30 min to prepare a dark brown precipitate. Theproduct was separated, washed several times with distilled water andethanol, and dried at 80° C. for 12 h. Some amount of the MnO₂ powderwas then subjected to the direct transfer treatment to obtaingraphene-encapsulated MnO₂ particles. Coated primary particles were thenmade into secondary particles according to similar procedures describedin Example 1.

Additionally, NaMnO₂ particles were synthesized by ball-milling amixture of Na₂CO₃ and MnO₂ (at a molar ratio of 1:2) for 12 h followedby heating at 870° C. for 10 h. The resulting NaMnO₂ particles were thensubjected to ball-milling in the presence of MCMB particles to preparegraphene encapsulated NaMnO₂ particles.

The MnO₂ particles, with or without graphene encapsulation, are alsoincorporated in alkaline Zn/MnO₂ cells. Graphene encapsulation was foundto dramatically increase the cycle life of this type of cell. TheZn-graphene/MnO₂ battery is composed of a graphene/MnO₂-based cathode(with an optional cathode current collector and an optional conductivefiller), a Zn metal or alloy-based anode (with an optional anode currentcollector), and an aqueous electrolyte (e.g. a mixture of a mild ZnSO₄or Zn(NO₃)₂ with MnSO₄ in water).

EXAMPLE 15 Layered Zinc Hydroxide Salts Encapsulated by Graphene Sheetsas the Hybrid Cathode Material

The structural arrangements of dodecyl sulfate (DS) anions in theinterlayer space of layered zinc hydroxide salts (LZH-DS) and of thestructure of zinc hydroxide layers were investigated. As-prepared,highly crystalline LZH-DS has a basal spacing of 31.5 Å (3.15 nm). Aftertreatment with methanol at room temperature, zinc hydroxide layersshrank to form two new layered phases with basal spacings of 26.4 and24.7 Å. The shrinking was accompanied by a decrease in the content of DSanions in the interlayer space, indicating a change in the alignment ofthe intercalated anions and a decrease in the charge density of the zinchydroxide layers. This study indicates that tetrahedra Zn ions can bereversibly removed from the hydroxide layers, with the octahedrallycoordinated Zn ions left unaffected. This result suggests that layeredzinc hydroxide can be used as a Zn intercalation compound. In thepresent investigation, layered zinc hydroxide particles were alsosubjected to ball milling in the presence of natural graphite particles,resulting in the formation of graphene-encapsulated zinc hydroxideparticles, which were then further embraced by RGO sheets to makesecondary particles. It was discovered that graphene encapsulationimparts high-rate capability to the layered zinc hydroxide when used asa cathode active material of a Zn metal cell.

EXAMPLE 16 Preparation and Electrochemical Testing of Various BatteryCells

For most of the anode and cathode active materials investigated, weprepared lithium-ion cells or lithium metal cells using the conventionalslurry coating method. A typical anode composition includes 85 wt. %active material (e.g., graphene-encapsulated, Si or Co₃O₄ particles), 7wt. % acetylene black (Super-P), and 8 wt. % polyvinylidene fluoridebinder (PVDF, 5 wt. % solid content) dissolved inN-methyl-2-pyrrolidinoe (NMP). After coating the slurries on Cu foil,the electrodes were dried at 120° C. in vacuum for 2 h to remove thesolvent. With the instant method, typically no binder resin is needed orused, saving 8% weight (reduced amount of non-active materials). Cathodelayers (e.g. LFP, NCM, LiCoO₂, etc.) are made in a similar manner (usingAl foil as the cathode current collector) using the conventional slurrycoating and drying procedures. An anode layer, separator layer (e.g.Celgard 2400 membrane), and a cathode layer are then laminated togetherand housed in a plastic-Al envelop. The cell is then injected with 1 MLiPF₆ electrolyte solution dissolved in a mixture of ethylene carbonate(EC) and diethyl carbonate (DEC) (EC-DEC, 1:1 v/v). In some cells, ionicliquids were used as the liquid electrolyte. The cell assemblies weremade in an argon-filled glove-box.

The cyclic voltammetry (CV) measurements were carried out using an Arbinelectrochemical workstation at a typical scanning rate of 1 mV/s. Inaddition, the electrochemical performances of various cells were alsoevaluated by galvanostatic charge/discharge cycling at a current densityof from 50 mA/g to 10 A/g. For long-term cycling tests, multi-channelbattery testers manufactured by LAND were used.

In lithium-ion battery industry, it is a common practice to define thecycle life of a battery as the number of charge-discharge cycles thatthe battery suffers 20% decay in capacity based on the initial capacitymeasured after the required electrochemical formation.

Shown in FIG. 4 are the charge-discharge cycling behaviors of 3 lithiumcells all featuring Co₃O₄ particle-based anodes: (a) containingun-protected Co₃O₄ particles, (b) graphene-encapsulated Co₃O₄ primaryparticles produced by the instant direct transfer method; and (c)graphene-embraced particulates (secondary particles) ofgraphene-encapsulated Co₃O₄ primary particles. These data have clearlydemonstrated the surprising result that the presently inventedgraphene-embraced secondary particles of graphene-encapsulated Co₃O₄primary particles, when implemented as an anode active material, deliverthe very best battery cycling behavior, even better than that of abattery having graphene-encapsulated primary Co₃O₄ particles as theanode active material. In contrast, the battery having un-protectedCo₃O₄ particles as the anode active material exhibit rapid capacitydecay upon repeated charges and discharges.

FIG. 5 shows the charge-discharge cycling behaviors 3 lithium cellsfeaturing SnO₂ particle-based anodes: the first containing un-protectedSnO₂ particles, second containing graphene-encapsulated primary SnO₂particles produced by the instant direct transfer method, and the thirdcontaining graphene-embraced particulates of graphene-encapsulatedprimary particles. Again, the instant method of particulate formationleads to a lithium battery that exhibits a significantly more stablecycling behavior.

FIG. 6 shows the charge-discharge cycling behaviors of 3 lithium cellsfeaturing micron-scaled (3 μm) Si particle-based anodes: a) containingun-protected Si particles, b) graphene-embraced primary Si particlesproduced by the direct transfer method, and c) graphene-embracedparticulates of graphene-encapsulated Si particles produced by theinstant direct transfer method (Si particles themselves being thegraphene-peeling agent), followed by slurry spray-drying. Again, quiteunexpectedly, graphene-embraced particulates containinggraphene-encapsulated Si_(primary) particles produced by the instantdirect transfer method imparts significantly better battery cyclingperformance as compared to the electrode containing graphene-embraced Siprimary particles.

FIG. 7 shows the discharge capacity values (mAh/g, based on compositeweight) of 3 lithium cells featuring lithium iron phosphate (LFP)particle-based cathodes, plotted as a function of discharge C-rates:first one containing un-protected LFO particles (mixed with 12% byweight carbon), second one containing graphene-encapsulated carbon-addedLFP primary particles produced by the instant direct transfer method (4%graphene+8% C), and third one RGO-embraced particulates ofgraphene-encapsulated primary LFP particles. It may be noted that theC-rates are commonly used in the arts of lithium batteries tocharacterize the ability of a battery or battery electrode to undergofast charge or discharge without a significant capacity decay. Herein,by definition, 1 C rate=complete discharge in 1 hour or 60 minute; 5 Crate=complete discharge in 60/5=12 minutes; 0.1 C rate=completedischarge in 60/0.1=600 minutes or 10 hours. These data summarized inFIG. 7 have clearly demonstrated the surprising effectiveness of usingthe double-level graphene embracing/encapsulation protection strategy inminimizing capacity reduction when the battery is discharged in highrates.

FIG. 8 shows the charge-discharge cycling behaviors of 3 lithium cellsfeaturing LiV₂O₅ nanorod-based cathodes: a) containing RGO-embracedparticulates of graphene-encapsulated LiV₂O₅ nanorods, b)graphene-embraced LiV₂O₅ nanorods produced by the direct transfer method(approximately 5% graphene+7% C), and c) LiV₂O₅ nanorods protected by acarbon matrix. These results have demonstrated that graphene-embracedsecondary particles containing graphene-encapsulated LiV₂O₅ nanorods(primary particles) produced by the direct transfer method lead to themost stable battery cycling behavior.

FIG. 4, FIG. 5, FIG. 6, FIG. 7, and FIG. 8 are but a few examples of themassive amount of data that demonstrate the surprisingly superiorcycling performances of lithium batteries featuring the presentlyinvented graphene-encapsulated electrode active material particles.Similar results have been obtained with other types of batteries, suchas other lithium metal secondary battery, lithium-sulfur battery,lithium-air battery, lithium-selenium battery, sodium-ion battery,sodium metal secondary battery, sodium-sulfur battery, sodium-airbattery, magnesium-ion battery, magnesium metal battery, aluminum-ionbattery, aluminum metal secondary battery, zinc-ion battery, zinc metalbattery, zinc-air battery, lithium-ion capacitors, and sodium-ioncapacitors.

The invention claimed is:
 1. A graphene-embraced particulate for use asa lithium-ion battery cathode active material, wherein said particulatecomprises a single or a plurality of graphene-encapsulated primaryparticles of a cathode active material, comprising a primary particle ofsaid cathode active material and multiple sheets of a first graphenematerial overlapped together to embrace or encapsulate said primaryparticle, and wherein said single or a plurality ofgraphene-encapsulated primary particles, along with an optionalconductive additive, are further embraced or encapsulated by multiplesheets of a second graphene material, wherein said first graphenematerial is the same as or different from said second graphene material,and wherein said first graphene and said second graphene material iseach in an amount from 0.01% to 20% by weight and said optionalconductive additive is in an amount from 0% to 50% by weight, all basedon the total weight of said particulate.
 2. The particulate of claim 1,wherein said particulate is spherical or ellipsoidal in shape.
 3. Theparticulate of claim 1, wherein said first graphene material or saidsecond graphene material comprises single-layer graphene or few-layergraphene, wherein said few-layer graphene is defined as a graphene sheetor platelet formed of 2-10 graphene planes.
 4. The particulate of claim1, wherein said first graphene material or said second graphene materialis selected from pristine graphene, graphene oxide, reduced grapheneoxide, graphene fluoride, graphene chloride, graphene bromide, grapheneiodide, hydrogenated graphene, nitrogenated graphene, chemicallyfunctionalized graphene, or a combination thereof.
 5. The particulate ofclaim 1, wherein said first graphene material is different than saidsecond graphene material.
 6. The particulate of claim 1, wherein firstgraphene material contains pristine graphene and said second graphenematerial is selected from graphene oxide, reduced graphene oxide,graphene fluoride, graphene chloride, graphene bromide, graphene iodide,hydrogenated graphene, nitrogenated graphene, chemically functionalizedgraphene, or a combination thereof.
 7. The particulate of claim 1,wherein first graphene material contains pristine graphene or a firstchemically functionalized graphene and said second graphene material isselected from graphene oxide, reduced graphene oxide, graphene fluoride,graphene chloride, graphene bromide, graphene iodide, hydrogenatedgraphene, nitrogenated graphene, a second chemically functionalizedgraphene, or a combination thereof, wherein said first chemicallyfunctionalized graphene is different than the second chemicallyfunctionalized graphene.
 8. The particulate of claim 1, wherein saidcathode active material is selected from an inorganic material, anorganic or polymeric material, a metal oxide/phosphate/sulfide, or acombination thereof.
 9. The particulate of claim 8, wherein said metaloxide/phosphate/sulfide is selected from a lithium cobalt oxide, lithiumnickel oxide, lithium manganese oxide, lithium vanadium oxide,lithium-mixed metal oxide, lithium iron phosphate, lithium manganesephosphate, lithium vanadium phosphate, lithium mixed metal phosphate,sodium cobalt oxide sodium nickel oxide, sodium manganese oxide, sodiumvanadium oxide, sodium-mixed metal oxide, sodium iron phosphate, sodiummanganese phosphate, sodium vanadium phosphate, sodium mixed metalphosphate, transition metal sulfide, lithium polysulfide, sodiumpolysulfide, magnesium polysulfide, or a combination thereof.
 10. Theparticulate of claim 1, wherein said cathode active material is selectedfrom sulfur, sulfur compound, sulfur-carbon composite, sulfur-polymercomposite, lithium polysulfide, transition metal dichalcogenide, atransition metal trichalcogenide, or a combination thereof.
 11. Theparticulate of claim 8, wherein said inorganic material is selected fromTiS₂, TaS₂, MoS₂, NbSe₃, MnO₂, COO₂, an iron oxide, a vanadium oxide, ora combination thereof.
 12. The particulate of claim 8, wherein saidmetal oxide/phosphate/sulfide contains a vanadium oxide selected fromthe group consisting of VO₂, Li_(x)VO₂, V₂O₅, Li_(x)V₂O₅, V₃O₈,Li_(x)V₃O₈, Li_(x)V₃O₇, V₄O₉, Li_(x)V₄O₉, V₆O₁₃, Li_(x)V₆O₁₃, theirdoped versions, their derivatives, and combinations thereof, wherein0.1<x<5.
 13. The particulate of claim 8, wherein said metaloxide/phosphate/sulfide is selected from a layered compound LiMO₂,spinel compound LiM₂O₄, olivine compound LiMPO₄, silicate compoundLi₂MSiO₄, tavorite compound LiMPO₄F, borate compound LiMBO₃, or acombination thereof, wherein M is a transition metal or a mixture ofmultiple transition metals.
 14. The particulate of claim 8, wherein saidinorganic material is selected from: (a) bismuth selenide or bismuthtelluride, (b) transition metal dichalcogenide or trichalcogenide, (c)sulfide, selenide, or telluride of niobium, zirconium, molybdenum,hafnium, tantalum, tungsten, titanium, cobalt, manganese, iron, nickel,or a transition metal; (d) boron nitride, or (e) a combination thereof.15. The particulate of claim 8, wherein said organic material orpolymeric material is selected from poly(anthraquinonyl sulfide) (PAQS),a lithium oxocarbon, 3,4,9,10-perylenetetracarboxylic dianhydride(PTCDA), poly(anthraquinonyl sulfide), pyrene-4,5,9,10-tetraone (PYT),polymer-bound PYT, quino(triazene), redox-active organic material,tetracyanoquinodimethane (TCNQ), tetracyanoethylene (TCNE),2,3,6,7,10,11-hexamethoxytriphenylene (HMTP), poly(5-amino-1,4-dyhydroxyanthraquinone) (PADAQ), phosphazene disulfide polymer ([(NPS₂)₃]n),lithiated 1,4,5,8-naphthalenetetraol formaldehyde polymer,hexaazatrinaphtylene (HATN), hexaazatriphenylene hexacarbonitrile(HAT(CN)₆), 5-benzylidene hydantoin, isatine lithium salt, pyromelliticdiimide lithium salt, tetrahydroxy-p-benzoquinone derivatives (THQLi₄),N,N′-diphenyl-2,3,5,6-tetraketopiperazine (PHP),N,N′-diallyl-2,3,5,6-tetraketopiperazine (AP),N,N′-dipropyl-2,3,5,6-tetraketopiperazine (PRP), a thioether polymer, aquinone compound, 1,4-benzoquinone, 5,7,12,14-pentacenetetrone (PT),5-amino-2,3-dihydro-1,4-dyhydroxy anthraquinone (ADDAQ),5-amino-1,4-dyhydroxy anthraquinone (ADAQ), calixquinone, Li₄C₆O₆,Li₂C₆O₆, Li₆C₆O₆, or a combination thereof.
 16. The particulate of claim15, wherein said thioether polymer is selected frompoly[methanetetryl-tetra(thiomethylene)] (PMTTM),poly(2,4-dithiopentanylene) (PDTP), a polymer containingpoly(ethene-1,1,2,2-tetrathiol) (PETT) as a main-chain thioetherpolymers, a side-chain thioether polymer having a main-chain consistingof conjugating aromatic moieties, and having a thioether side chain as apendant, poly(2-phenyl-1,3-dithiolane) (PPDT),poly(1,4-di(1,3-dithiolan-2-yl)benzene) (PDDTB),poly(tetrahydrobenzodithiophene) (PTHBDT),poly[1,2,4,5-tetrakis(propylthio)benzene](PTKPTB, orpoly[3,4(ethylenedithio)thiophene] (PEDTT).
 17. The particulate of claim8, wherein said organic material contains a phthalocyanine compoundselected from copper phthalocyanine, zinc phthalocyanine, tinphthalocyanine, iron phthalocyanine, lead phthalocyanine, nickelphthalocyanine, vanadyl phthalocyanine, fluorochromium phthalocyanine,magnesium phthalocyanine, manganous phthalocyanine, dilithiumphthalocyanine, aluminum phthalocyanine chloride, cadmiumphthalocyanine, chlorogallium phthalocyanine, cobalt phthalocyanine,silver phthalocyanine, a metal-free phthalocyanine, a chemicalderivative thereof, or a combination thereof.
 18. The particulate ofclaim 1, wherein said cathode active material contains a mixture of anorganic material and an inorganic material or a metaloxide/phosphate/sulfide.
 19. The particulate of claim 1, wherein saidprimary particles of a cathode active material have a size from 10 nm to1 μm.
 20. The particulate of claim 1, wherein said primary particles ofa cathode active material have a size from 10 nm to 100 nm.
 21. Theparticulate of claim 1, wherein said conductive additive is selectedfrom amorphous carbon, CVD carbon, carbonized resin, expanded graphiteplatelet, carbon nanotube, carbon nanofiber, carbon fiber, graphitefiber, pitch, coke, carbon black, acetylene black, activated carbon,pitch-derived soft carbon (graphitizable carbon), pitch-derived hardcarbon (non-graphitizable carbon), natural graphite particle, artificialgraphite particle, electron-conducting polymer, lithium ion-conductingpolymer, or a combination thereof, wherein said conductive additive isin electronic contact with said graphene-encapsulated primary particle.22. The particulate of claim 21, wherein said carbonized resin isobtained from pyrolyzation of a polymer selected from the groupconsisting of phenol-formaldehyde, polyacrylonitrile, styrene-basedpolymers, cellulosic polymers, epoxy resins, and combinations thereof.23. A mass of multiple particulates as defined in claim
 1. 24. A lithiumbattery cathode electrode containing a mass of multiple particulates ofclaim 1 and optional conductive filler and binder.
 25. A lithium batterycontaining the cathode electrode of claim
 24. 26. A battery electrodecontaining said graphene-embraced particulates produced in claim 1 as ancathode active material, wherein said battery is a lithium-ion battery,lithium metal secondary battery, lithium-sulfur battery, lithium-airbattery, lithium-selenium battery, sodium-ion battery, sodium metalsecondary battery, sodium-sulfur battery, sodium-air battery,magnesium-ion battery, magnesium metal battery, aluminum-ion battery,aluminum metal secondary battery, zinc-ion battery, zinc metal battery,or zinc-air battery.